Aluminum with grain refiners, and methods for making and using the same

ABSTRACT

We have developed a scalable approach to directly incorporate grain-refining nanoparticles into conventional hot-tear-susceptible pure aluminum or aluminum alloy powders. These aluminum alloy powders may be additively manufactured into high-strength, crack-free aluminum alloys with fine equated microstructures by incorporating nanoparticle nucleants to control solidification during additive manufacturing. Some variations provide an additively manufactured aluminum alloy comprising aluminum and at least one grain-refining element, wherein the additively manufactured aluminum alloy has a microstructure with equated grains. Pure aluminum or aluminum alloys, combined with grain refiners, are useful in many processes beyond additive manufacturing. Some variations provide an aluminum alloy comprising aluminum and grain-refining nanoparticles selected from zirconium, tantalum, niobium, or titanium, wherein the aluminum alloy has a microstructure that is substantially crack-free with equated grains.

PRIORITY DATA

This patent application is a continuation patent application of U.S. patent application Ser. No. 15/880,466, filed on Jan. 25, 2018, which claims priority to U.S. Provisional Patent App. No. 62/452,989, filed on Feb. 1, 2017, each of which is hereby incorporated by reference herein.

FIELD OF THE INVENTION

The present invention generally relates to metal alloys with grain refiners, and methods of making and using the same.

BACKGROUND OF THE INVENTION

Aluminum and its alloys are characterized by a relatively low density, high electrical and thermal conductivities, and a resistance to corrosion in some common environments, including the ambient atmosphere. Recent attention has been given to alloys of aluminum as engineering materials for transportation to reduce fuel consumption due to high specific strength. The mechanical strength of aluminum may be enhanced by cold work and by alloying. Principal alloying elements include copper, magnesium, silicon, zinc, and manganese.

Generally, aluminum alloys are classified as either cast or wrought. Some common cast, heat-treatable aluminum alloys include Al 295.0 and Al 356.0 (the decimal point denotes a cast alloy). Wrought alloys include heat-treatable alloys (e.g., Al 2104, Al 6061, and Al 7075) and non-heat-treatable alloys (e.g., Al 1100, Al 3003, and Al 5052). Wrought, heat-treatable aluminum alloys are generally superior in mechanical strength compared to other types of Al alloys.

Metal-based additive manufacturing, or three-dimensional (3D) printing, has applications in many industries, including the aerospace and automotive industries. Building up metal components layer by layer increases design freedom and manufacturing flexibility, thereby enabling complex geometries while eliminating traditional economy-of-scale constraints. However, currently only a few alloys, the most relevant being AlSi10Mg, TiAl6V4, CoCr, and Inconel 718, can be reliably printed. The vast majority of the more than 5,500 alloys in use today cannot be additively manufactured because the melting and solidification dynamics during the printing process lead to intolerable microstructures with large columnar grains and cracks. 3D-printable metal alloys are limited to those known to be easily weldable. The limitations of the currently printable alloys, especially with respect to specific strength, fatigue life, and fracture toughness, have hindered metal-based additive manufacturing. See Martin et al., “3D printing of high-strength aluminium alloys,” Nature vol. 549, pages 365-369.

Specifically regarding aluminum alloys, the only printable aluminum alloys are based on the binary Al—Si system and tend to converge around a yield strength of approximately 200 MPa with a low ductility of 4%. The exception is Scalmalloy, which relies on alloying additions of scandium, a rare high-cost metal. In contrast, most aluminum alloys used in automotive, aerospace, and consumer applications are wrought alloys of the 2000, 5000, 6000, or 7000 series, which can exhibit strengths exceeding 400 MPa and ductility of more than 10% but cannot currently be additively manufactured. These systems have low-cost alloying elements (Cu, Mg, Zn, and Si) carefully selected to produce complex strengthening phases during subsequent ageing. These same elements promote large solidification ranges, leading to hot tearing (cracking) during solidification—a problem that has been difficult to surmount for more than 100 years since the first age-hardenable alloy, duralumin, was developed.

In particular, during solidification of these alloys, the primary equilibrium phase solidifies first at a different composition from the bulk liquid. This mechanism results in solute enrichment in the liquid near the solidifying interface, locally changing the equilibrium liquidus temperature and producing an unstable, undercooled condition. As a result, there is a breakdown of the solid-liquid interface leading to cellular or dendritic grain growth with long channels of interdendritic liquid trapped between solidified regions. As temperature and liquid volume fraction decrease, volumetric solidification shrinkage and thermal contraction in these channels produces cavities and hot tearing cracks which may span the entire length of the columnar grain and can propagate through additional intergranular regions. Note that aluminum alloys Al 7075 and Al 6061 are highly susceptible to the formation of such cracks, due to a lack of processing paths to produce fine equated grains.

Fine equated microstructures accommodate strain in the semi-solid state by suppressing coherency that locks the orientation of these solid dendrites, thereby promoting tear resistance. Producing equated structures requires large amounts of undercooling, which has thus far proven difficult in additive processes where high thermal gradients arise from rastering of a direct energy source in an arbitrary geometric pattern.

What is needed is an approach to control solidification microstructure by promoting nucleation of new grains. What are specifically desired are aluminum alloys with equated-grain microstructures that are substantially free of cracks.

SUMMARY OF THE INVENTION

The present invention addresses the aforementioned needs in the art, as will now be summarized and then further described in detail below.

Some variations provide an aluminum alloy comprising:

(a) at least 80 wt % aluminum; and

(b) grain-refining nanoparticles comprising an element selected from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing,

wherein the aluminum alloy has a microstructure that is substantially crack-free with equated grains.

In some embodiments, the aluminum is present in a concentration of at least 90 wt %, at least 99 wt %, or at least 99.9 wt %. In certain embodiments, the aluminum alloy consists essentially of the aluminum and the grain-refining nanoparticles. Note that the aluminum may be in the form of pure aluminum, except for the presence of the grain-refining nanoparticles in the composition. That is, rather than starting with an aluminum alloy that is then combined with one or more grain-refining nanoparticles, some embodiments start with pure aluminum and add one or more grain-refining nanoparticles to the pure aluminum. See Example 1 for an illustration.

In some embodiments, the grain-refining nanoparticles are present in a concentration of at least 0.01 vol %, at least 0.1 vol %, at least 1 vol %, or at least 5 vol %.

In some embodiments, the aluminum alloy contains inclusions of an aluminide selected from the group consisting of Al₃Ta, Al₃Zr, Al₃Nb, Al₃Ti, and combinations thereof.

Some variations of the invention provide an additively manufactured aluminum alloy comprising:

(a) at least 80 wt % aluminum; and

(b) at least one grain-refining element selected from the group consisting of zirconium, tantalum, niobium, titanium, boron, tungsten, carbon, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing,

wherein the additively manufactured aluminum alloy has a microstructure with equated grains.

In some embodiments, the aluminum is present in a concentration of at least 90 wt %, least 99 wt %, or at least 99.9 wt %. In certain embodiments, the additively manufactured aluminum alloy consists essentially of the aluminum and the at least one grain-refining element. Again, the aluminum may be in the form of pure aluminum.

In some embodiments, at least one grain-refining element is selected from the group consisting of Al₃Zr, Al₃Ta, Al₃Nb, Al₃Ti, TiB, TiB₂, WC, AlB, and combinations thereof. In some embodiments, at least one grain-refining element is in the form of nanoparticles.

The additively manufactured aluminum alloy may have a microstructure that is substantially crack-free. Additionally, the microstructure may be substantially free of porous void defects.

The additive manufacturing process may be selected from the group consisting of selective laser melting, energy-beam melting, laser engineered net shaping, and combinations thereof, for example.

In some embodiments, the additively manufactured aluminum alloy microstructure has a crystallographic texture that is not solely oriented in an additive-manufacturing build direction. For example, the additively manufactured aluminum alloy microstructure may contain a plurality of dendrite layers having differing primary growth-direction angles with respect to each other.

Other variations provide a functionalized aluminum powder comprising pure aluminum and grain-refining nanoparticles. The functionalized aluminum powder is the starting feedstock to produce an aluminum alloy, such as an additively manufactured aluminum alloy, as summarized above.

In some embodiments of the functionalized aluminum powder, the grain-refining nanoparticles are from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing. In some embodiments, the grain-refining nanoparticles are present in a concentration of at least 0.01 vol %.

BRIEF DESCRIPTION OF THE FIGURES

FIG. 1 is an SEM image of Al 7075 powder with TiB₂ nanoparticles (scale bar 5 μm), in some embodiments.

FIG. 2 is an SEM image of TiAl6V4 powder with ZrH₂ nanoparticles (scale bar 25 μm), in some embodiments.

FIG. 3 is an SEM image of Al 7075 powder with WC (tungsten carbide) nanoparticles (scale bar 5 μm), in some embodiments.

FIG. 4 is an SEM image of AlSi10Mg powder with WC nanoparticles (scale bar 5 μm), in some embodiments.

FIG. 5 is an SEM image of Fe powder with TiC nanoparticles (scale bar 1 μm), in some embodiments.

FIG. 6A shows an image of non-grain-refined pure aluminum, revealing large columnar grains and cracks.

FIG. 6B shows an image of grain-refined aluminum with Ta particles, revealing fine equated growth and a substantially crack-free microstructure, in Example 1 herein.

FIG. 7A shows an image of non-grain-refined aluminum alloy Al 7075, revealing columnar grains and significant cracking.

FIG. 7B shows an image of grain-refined aluminum alloy Al 7075 with Zr particles, revealing fine equated grains and a substantially crack-free microstructure, in Example 2 herein.

FIG. 8A shows a magnified (scale bar 25 μm), polished and etched SEM image of non-grain-refined aluminum alloy Al 7075.

FIG. 8B shows a magnified (scale bar 25 μm), polished and etched SEM image of grain-refined aluminum alloy, Al 7075+Zr, in Example 2 herein.

FIG. 9 is a stress-strain curve of a functionalized aluminum alloy versus two non-functionalized aluminum alloys, indicating significantly improved mechanical properties due to suppression of cracking in Al 7075+Zr-T6, in Example 3 herein.

FIG. 10A shows an image of non-grain-refined aluminum alloy Al 6061, revealing significant cracking.

FIG. 10B shows an image of grain-refined aluminum alloy Al 6061 with Zr particles, revealing fine equated grains and a substantially crack-free microstructure, in Example 4 herein.

DETAILED DESCRIPTION OF EMBODIMENTS OF THE INVENTION

The compositions, structures, systems, and methods of the present invention will be described in detail by reference to various non-limiting embodiments.

This description will enable one skilled in the art to make and use the invention, and it describes several embodiments, adaptations, variations, alternatives, and uses of the invention. These and other embodiments, features, and advantages of the present invention will become more apparent to those skilled in the art when taken with reference to the following detailed description of the invention in conjunction with the accompanying drawings.

As used in this specification and the appended claims, the singular forms “a,” “an,” and “the” include plural referents unless the context clearly indicates otherwise. Unless defined otherwise, all technical and scientific terms used herein have the same meaning as is commonly understood by one of ordinary skill in the art to which this invention belongs.

Unless otherwise indicated, all numbers expressing conditions, concentrations, dimensions, and so forth used in the specification and claims are to be understood as being modified in all instances by the term “about.” Accordingly, unless indicated to the contrary, the numerical parameters set forth in the following specification and attached claims are approximations that may vary depending at least upon a specific analytical technique.

The term “comprising,” which is synonymous with “including,” “containing,” or “characterized by” is inclusive or open-ended and does not exclude additional, unrecited elements or method steps. “Comprising” is a term of art used in claim language which means that the named claim elements are essential, but other claim elements may be added and still form a construct within the scope of the claim.

As used herein, the phrase “consisting of” excludes any element, step, or ingredient not specified in the claim. When the phrase “consists of” (or variations thereof) appears in a clause of the body of a claim, rather than immediately following the preamble, it limits only the element set forth in that clause; other elements are not excluded from the claim as a whole. As used herein, the phrase “consisting essentially of” limits the scope of a claim to the specified elements or method steps, plus those that do not materially affect the basis and novel characteristic(s) of the claimed subject matter.

With respect to the terms “comprising,” “consisting of,” and “consisting essentially of,” where one of these three terms is used herein, the presently disclosed and claimed subject matter may include the use of either of the other two terms, except when used in Markush groups. Thus in some embodiments not otherwise explicitly recited, any instance of “comprising” may be replaced by “consisting of” or, alternatively, by “consisting essentially of.”

The present invention provides aluminum alloy systems that utilize grain refiners to give a unique microstructure for the aluminum alloy. The grain refiners are designed with specific compositions for a given aluminum alloy and can be incorporated at higher concentrations than previously possible due to assembly of the grain refiners on the surface of a base aluminum alloy powder. This approach enables the production of aluminum alloys that were previously difficult to process.

Some variations provide routes to controlled solidification of materials which are generally difficult or impossible to process otherwise. The principles disclosed herein may be applied to additive manufacturing as well as joining techniques, such as welding. Certain unweldable metals, such as high-strength aluminum alloys (e.g., aluminum alloys Al 7075, Al 7050, or Al 2199) would be excellent candidates for additive manufacturing but normally suffer from hot cracking. The methods disclosed herein allow these alloys to be processed with significantly reduced cracking tendency.

Some variations relate specifically to additive manufacturing of aluminum alloys. Additive manufacturing has been previously limited to weldable or castable alloys of aluminum. This invention eliminates that limitation and enables additive manufacturing of a variety of high-strength and unweldable aluminum alloys by utilizing grain refinement to induce equated microstructures which can eliminate hot cracking during processing.

Potential applications include improved tooling, replacement of steel or titanium components at lower weight, full topological optimization of aluminum components, low-cost replacement for out-of-production components, and replacement of existing additively manufactured aluminum systems.

Currently the only reasonably available aluminum alloys are castable Al—Si alloys, which peak in strength around 220 MPa. A high-cost alternative, Scalmalloy, is available with a reported yield of 450 MPa; however, the addition of scandium makes Scalmalloy an undesirable system. The present invention expands beyond scandium to more cost-effective grain-refining elements and demonstrates effectiveness across many aluminum alloy systems.

In particular, methods of this invention may be employed to produce a unique microstructure in a wide variety of alloy systems. Incorporation of previously impossible concentrations and types of grain refiners is possible, in this disclosure, due to grain-refining elements being disposed on surfaces of base alloy powder. This process utilizes functionalization to incorporate grain refiners directly at the site of melting, negating the need for expensive processing and making use of commercially available alloy powders. This technique is in contrast to incorporation of grain refiners directly into a powder, which requires extremely high temperatures during gas atomization which can be difficult to handle due to volatility of certain alloying elements in aluminum alloys (including Zn, Mg, and Li), and can be damaging to equipment due to the high reactivity of elements in aluminum alloys.

Some embodiments of the present invention utilize materials, methods, and principles described in commonly owned U.S. patent application Ser. No. 15/209,903, filed Jul. 14, 2016, and/or commonly owned U.S. patent application Ser. No. 15/808,877, filed Nov. 9, 2017, each of which is hereby incorporated by reference herein. For example, certain embodiments utilize functionalized powder feedstocks as described in U.S. patent application Ser. No. 15/209,903. The present disclosure is not limited to those functionalized powders. This specification also hereby incorporates by reference herein Martin et al., “3D printing of high-strength aluminium alloys,” Nature vol. 549, pages 365-369 and supplemental online content (extended data), Sep. 21, 2017, in its entirety.

In some embodiments, micropowders are functionalized with assembled nanoparticles that are lattice-matched to a primary or secondary solidifying phase in the parent material, or that may react with elements in the micropowder to form a lattice-matched phase to a primary or secondary solidifying phase in the parent material. In certain embodiments, mixtures of assembled nanoparticles may react with each other or in some fashion with the parent material, to form a lattice-matched material having the same or similar function. For example, alloy powder feedstock particles may be decorated with lattice-matched nanoparticles that heterogeneously nucleate the primary equilibrium phases during cooling of the melt pool. Further description of micropowders that are functionalized with nanoparticles, in various embodiments, is found below.

FIGS. 1 to 5 are scanning electron microscopy (SEM) images of exemplary micropowders that are functionalized with assembled nanoparticles. FIG. 1 shows Al 7075 powder 110 functionalized with TiB₂ nanoparticles 120 (scale bar 5 μm), resulting in nanofunctionalized metal powder 100. FIG. 2 shows TiAl6V4 powder 210 functionalized with ZrH₂ nanoparticles 220 (scale bar 25 μm), resulting in nanofunctionalized metal powder 200. FIG. 3 shows Al 7075 powder 310 functionalized with WC (tungsten carbide) nanoparticles 320 (scale bar 5 μm), resulting in nanofunctionalized metal powder 300. FIG. 4 shows AlSi10Mg powder 410 functionalized with WC nanoparticles 420 (scale bar 5 μm), resulting in nanofunctionalized metal powder 400. FIG. 5 shows iron powder 510 functionalized with TiC nanoparticles 520 (scale bar 1 μm) by dry mixing, resulting in nanofunctionalized metal powder 500.

By providing a high density of low-energy-barrier heterogeneous nucleation sites ahead of the solidification front, the critical amount of undercooling needed to induce equated growth is decreased. This allows for a fine equated grain structure that accommodates strain and prevents cracking under otherwise identical solidification conditions. Additive manufacturing of previously unattainable high-performance alloys, such as Al 7075 or Al 6061, is made possible with improved properties over currently available systems.

In preferred embodiments, during melting, the functionalized particles are incorporated into the melt and aid in the nucleation of new grains due to lattice matching, decreasing the critical amount of undercooling necessary for nucleation. In the absence of grain refiners, the high thermal gradient produced during additive manufacturing induces columnar growth. This is a serious problem during manufacturing of crack-susceptible metal or alloy systems. The columnar growth traps interdendritic liquid and leads to cavitation and cracking. Forcing equated growth decreases the coherency of dendrites and enables a reduced crack tendency. A dendrite is a characteristic tree-like structure of crystals produced by faster growth of crystals along energetically favorable crystallographic directions as molten metal freezes.

Some variations provide an aluminum alloy comprising:

(a) at least 80 wt % aluminum;

(b) copper;

(c) magnesium;

(d) at least one of zinc or silicon; and

(e) grain-refining nanoparticles comprising an element selected from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing,

wherein the aluminum alloy preferably has a microstructure that is substantially crack-free with equated grains.

In some embodiments, copper is present in a concentration from about 0.1 wt % to about 10 wt %. In these or other embodiments, magnesium is present in a concentration from about 0.1 wt % to about 10 wt %. In these or other embodiments, at least one of zinc or silicon is present in a concentration from about 0.1 wt % to about 10 wt %. In some embodiments, the aluminum alloy further comprises chromium. In some embodiments, scandium is not present in the aluminum alloy.

An aluminum alloy microstructure that is “substantially crack-free” means that at least 99.9 vol % of the aluminum alloy contains no linear or tortuous cracks that are greater than 0.1 microns in width and greater than 10 microns in length. In other words, to be considered a crack, a defect must be a void space that is at least 0.1 microns in width as well as at least 10 microns in length. A void space that has a length shorter than 10 microns but larger than 1 micron, regardless of width, can be considered a porous void (see below). A void space that has a length of at least 10 microns but a width shorter than 0.1 microns is a molecular-level gap that is not considered a defect.

Typically, a crack contains open space, which may be vacuum or may contain a gas such as air, CO₂, N₂, and/or Ar. A crack may also contain solid material different from the primary material phase of the aluminum alloy. These sorts of cracks containing material (other than gases) may be referred to as “inclusions.” The non-desirable material disposed within the inclusion may itself contain a higher porosity than the bulk material, may contain a different crystalline (or amorphous) phase of solid, or may be a different material altogether, arising from impurities during fabrication, for example. Large phase boundaries can also form inclusions.

The aluminum alloy microstructure may be substantially free of porous defects, in addition to being substantially crack-free. “Substantially free of porous defects” means at least 99 vol % of the aluminum alloy contains no porous voids having an effective diameter of at least 1 micron.

Preferably, at least 80 vol %, more preferably at least 90 vol %, even more preferably at least 95 vol %, and most preferably at least 99 vol % of the aluminum alloy contains no porous voids having an effective diameter of at least 1 micron. A porous void that has an effective diameter less than 1 micron is not typically considered a defect, as it is generally difficult to detect by conventional non-destructive evaluation. Also preferably, at least 90 vol %, more preferably at least 95 vol %, even more preferably at least 99 vol %, and most preferably at least 99.9 vol % of the aluminum alloy contains no larger porous voids having an effective diameter of at least 5 microns. For example, see the microstructure of FIG. 8B which contains porous voids (but contains no cracks).

Typically, a porous void contains open space, which may be vacuum or may contain a gas such as air, CO₂, N₂, and/or Ar. Porous voids may be reduced or eliminated, in some embodiments. For example, additively manufactured metal parts may be hot-isostatic-pressed to reduce residual porosity, and optionally to arrive at a final additively manufactured metal part that is substantially free of porous defects in addition to being substantially crack-free.

An aluminum alloy microstructure that has “equated grains” means that at least 90 vol %, preferably at least 95 vol %, and more preferably at least 99 vol % of the aluminum alloy contains grains that are roughly equal in length, width, and height. In preferred embodiments, at least 99 vol % of the aluminum alloy contains grains that are characterized in that there is less than 25%, preferably less than 10%, and more preferably less than 5% standard deviation in each of average grain length, average grain width, and average grain height. In the aluminum alloy, crystals of metal alloy form grains in the solid. Each grain is a distinct crystal with its own orientation. The areas between grains are known as grain boundaries. Within each grain, the individual atoms form a crystalline lattice. In this disclosure, equated grains result when there are many nucleation sites arising from grain-refining nanoparticles contained in the aluminum alloy microstructure.

The difference in microstructures that are substantially crack-free with equated grains, versus microstructures containing cracks and non-equated grains, can be seen in FIG. 6B versus FIG. 6A, as well as in FIG. 7B versus FIG. 7A, FIG. 8B versus FIG. 8A, and FIG. 10B versus FIG. 10A, as discussed in the Examples hereinbelow. Each of FIGS. 6B, 7B, 8B, and 10B show microstructures that are substantially crack-free with equated grains.

The grain-refining nanoparticles are preferably present in a concentration of at least 0.01 vol %, such as at least 0.1 vol %, at least 1 vol %, or at least 5 vol %. In various embodiments, the grain-refining nanoparticles are present in a concentration of about, or at least about, 0.1, 0.2, 0.5, 1, 2, 3, 4, 5, 6, 7, 8, 9, or 10 vol %. The concentration of the grain refiner may be varied by adjusting the amount of grain refiner functionalized on the powder surface, and/or by adjusting the concentration of functionalized micropowders versus non-functionalized micropowders in the final feedstock material.

The preferred concentration of grain refiner(s) will depend on the selected alloy and grain refiner. In certain alloys, grain refinement should be minimized to avoid potential detrimental interactions; however, some alloy systems such as Al 7075 can accommodate greater concentrations. Due to the ease of producing and processing the material, routine experimentation can be performed by a person of ordinary skill in the art to inform material selection and concentration for the grain-refining nanoparticles.

In certain embodiments, the aluminum alloy comprises zinc, and the grain-refining nanoparticles comprise an element selected from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing.

As a specific example pertaining to zirconium, the zirconium nanoparticles may be present as ZrH_(x) (x=0 to 4), i.e. in hydride form when x>0. An exemplary zirconium hydride is ZrH₂.

In certain embodiments, the aluminum alloy comprises silicon, and the grain-refining nanoparticles comprise an element selected from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing.

Generally speaking, the aluminum alloy, in addition to aluminum, may contain one or more alloying elements selected from the group consisting of Si, Fe, Cu, Ni, Mn, Mg, Cr, Zn, V, Ti, Bi, Ga, Pb, or Zr. Other alloying elements may be included in the aluminum alloy, such as (but not limited to) H, Li, Be, B, C, N, O, F, Na, P, S, Cl, K, Ca, Sc, Co, Zn, Ga, Ge, As, Se, Br, Rb, Sr, Y, Nb, Mo, Tc, Ru, Rh, Pd, Ag, Cd, In, Sn, Te, I, Cs, Ba, Hf, Ta, W, Re, Os, Ir, Pt, Au, Hg, Tl, Ce, Nd, and combinations thereof. These other alloying elements may function as grain refiners, as strength enhancers, as stability enhancers, or a combination thereof.

The base aluminum alloy (i.e., without the grain-refining nanoparticles) may be a wrought aluminum alloy selected from the 1000 series, 2000 series, 3000 series, 4000 series, 5000 series, 6000 series, 7000 series, 8000 series, or a combination thereof. Alternatively, or additionally, the base aluminum alloy may be a cast aluminum alloy.

The aluminum alloy may be selected from the 2000 series of aluminum alloys. The 2000 series of aluminum alloys includes aluminum alloys 2011, 2014, 2024, 2036, 2048, 2055, 2090, 2091, 2099, 2124, 2195, 2218, 2219, 2319, and 2618. In certain embodiments, the aluminum alloy is selected from aluminum alloy 2024, aluminum alloy 2219, or a combination thereof. The aluminum alloy provided herein may include any of the aforementioned Al alloys in combination with the grain-refining nanoparticles.

The aluminum alloy may be selected from the 6000 series of aluminum alloys. The 6000 series of aluminum alloys includes aluminum alloys 6005, 6009, 6010, 6060, 6061, 6063, 6063A, 6065, 6066, 6070, 6081, 6082, 6101, 6105, 6151, 6162, 6201, 6205, 6262, 6351, 6463, and 6951. In certain embodiments, the aluminum alloy is selected from aluminum alloy 6061, aluminum alloy 6063, or a combination thereof. The aluminum alloy provided herein may include any of the aforementioned Al alloys in combination with the grain-refining nanoparticles.

The aluminum alloy may be selected from the 7000 series of aluminum alloys. The 7000 series of aluminum alloys includes aluminum alloys 7005, 7034, 7039, 7049, 7050, 7068, 7072, 7075, 7175, 7079, 7116, 7129, 7178, and 7475. In certain embodiments, the aluminum alloy is selected from aluminum alloy 7050, aluminum alloy 7075, or a combination thereof. The aluminum alloy provided herein may include any of the aforementioned Al alloys in combination with the grain-refining nanoparticles.

The aluminum alloy provided herein may consist essentially of Al 7075 alloy in combination with the grain-refining nanoparticles. In other embodiments, the aluminum alloy may consist essentially of Al 6061 alloy in combination with the grain-refining nanoparticles.

In some embodiments in which the grain-refining nanoparticles comprise zirconium, the aluminum alloy contains inclusions comprising oxides, nitrides, hydrides, carbides, borides, or aluminides of zirconium, or a combination thereof. For example, the aluminum alloy may contain Al₃Zr (a zirconium aluminide) inclusions.

In some embodiments in which the grain-refining nanoparticles comprise tantalum, the aluminum alloy contains inclusions comprising oxides, nitrides, hydrides, carbides, borides, or aluminides of tantalum, or a combination thereof. For example, the aluminum alloy may contain Al₃Ta (a tantalum aluminide) inclusions.

In some embodiments in which the grain-refining nanoparticles comprise niobium, the aluminum alloy contains inclusions comprising oxides, nitrides, hydrides, carbides, borides, or aluminides of niobium, or a combination thereof. For example, the aluminum alloy may contain Al₃Nb (a niobium aluminide) inclusions.

In some embodiments in which the grain-refining nanoparticles comprise titanium, the aluminum alloy contains inclusions comprising oxides, nitrides, hydrides, carbides, borides, or aluminides of titanium, or a combination thereof. For example, the aluminum alloy may contain Al₃Ti (a titanium aluminide) inclusions.

The aluminum alloy may have a tensile strength of at least 400 MPa. In various embodiments, the aluminum alloy has a tensile strength of about, or at least about, 250, 300, 300, 350, 400, 450, or 500 MPa.

Some aluminum alloys provided herein are substantially free of porous defects, in addition to being substantially crack-free.

Some variations provide a method of making an aluminum alloy, the method comprising:

(a) obtaining microparticles containing aluminum, copper, magnesium, and at least one of zinc or silicon;

(b) chemically and/or physically disposing grain-refining nanoparticles on surfaces of the microparticles to generate functionalized microparticles, wherein the grain-refining nanoparticles comprise an element selected from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing; and

(c) processing the functionalized microparticles into an aluminum alloy,

wherein the aluminum alloy has a microstructure that is substantially crack-free with equated grains.

Some variations provide a method of making an aluminum alloy, the method comprising:

(a) obtaining microparticles containing aluminum, copper, magnesium, and at least one of zinc or silicon;

(b) chemically and/or physically disposing grain-refining nanoparticles on surfaces of the microparticles to generate functionalized microparticles, wherein the grain-refining nanoparticles comprise an element selected from the group consisting of zirconium, tantalum, niobium, titanium, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing; and

(c) processing the functionalized microparticles into an aluminum alloy,

wherein the aluminum alloy has a microstructure that is substantially crack-free with equated grains.

In various embodiments, step (b) includes pressing, binding, sintering, or a combination thereof. Step (b) may alternatively or additionally include metal injection molding, extruding, isostatic pressing, powder forging, spray forming, and/or other known techniques. The intermediate composition produced by step (b) may be referred to as a green body. In some embodiments, step (b) forms a powder feedstock. In certain embodiments, step (b) generates a wire or other geometric object containing the functionalized microparticles.

In various embodiments, processing in step (c) includes additive manufacturing, pressing, sintering, mixing, dispersing, friction stir welding, extrusion, binding (such as with a polymer binder), melting, semi-solid melting, sintering, casting, or a combination thereof. Melting may include induction melting, resistive melting, skull melting, arc melting, laser melting, electron beam melting, semi-solid melting, or other types of melting (including convention and non-conventional melt processing techniques). Casting may include centrifugal, pour, or gravity casting, for example. Sintering may include spark discharge, capacitive-discharge, resistive, or furnace sintering, for example. Mixing may include convection, diffusion, shear mixing, or ultrasonic mixing, for example. In certain embodiments, step (c) generates a wire or other geometric object containing the aluminum alloy.

Other variations of the present invention provide an additively manufactured aluminum alloy comprising:

(a) at least 80 wt % aluminum;

(b) at least one strengthening element selected from the group consisting of zinc, silicon, copper, magnesium, lithium, silver, titanium, chromium, manganese, iron, vanadium, bismuth, gallium, lead, and combinations thereof; and

(c) at least one grain-refining element selected from the group consisting of zirconium, tantalum, niobium, titanium, boron, tungsten, carbon, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing,

wherein the additively manufactured aluminum alloy has a microstructure with equated grains.

In various embodiments, at least one strengthening element, or a plurality of strengthening elements, is present in a concentration from about 0.01 wt % to about 20 wt %, such as about 0.1, 0.5, 1.0, 1.5, 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, or 15 wt %.

In some embodiments, at least one grain-refining element is selected from the group consisting of Al₃Zr, Al₃Ta, Al₃Nb, Al₃Ti, TiB, TiB₂, WC, AlB, and combinations thereof. At least one grain-refining element is preferably in the form of nanoparticles.

In some embodiments, at least one grain-refining element is lattice-matched to within ±5% compared to an alloy of the aluminum and the at least one strengthening element. Preferably, the grain-refining element is lattice-matched to within ±2%, more preferably to within ±0.5%, compared to an alloy of the aluminum and the at least one strengthening element.

In some embodiments, at least one grain-refining element is atomic density-matched to within ±25% compared to an alloy of the aluminum, the at least one strengthening element, and optionally an additional particulate. Preferably, the grain-refining element is atomic density-matched to within ±5%, more preferably to within ±0.5%, compared to an alloy of the aluminum and the at least one strengthening element, and optionally an additional particulate.

In some embodiments, nanoparticle compositions are targeted to a specific alloy using software that identifies matching crystallographic lattice spacing and density to provide a low-energy nucleation barrier on the basis of classical nucleation theory. For example, potential matches may be sorted by a combined set of constraints, such as (a) minimized lattice misfit, (b) similar atomic packing along matched crystallographic planes, (c) thermodynamic stability in the desired alloy, and/or (d) availability. In certain embodiments for aluminum alloys, hydrogen-stabilized zirconium particles are preferred due to stability in air and ability to decompose at the melting temperature, resulting in formation of a favorable Al₃Zr nucleant phase.

The aluminum alloy may be characterized by an average grain size of less than 1 millimeter, an average grain size of less than 10 microns, or an average grain size of less than 0.1 microns, for example. In various embodiments, the aluminum alloy may be characterized by an average grain size of about, or less than about, 500 microns, 400 microns, 300 microns, 200 microns, 100 microns, 50 microns, 25 microns, 10 microns, 5 microns, 2 microns, 1 micron, 0.5 microns, 0.2 microns, or 0.1 microns.

In some embodiments, the additively manufactured aluminum alloy microstructure is substantially crack-free. In these or other embodiments, the additively manufactured aluminum alloy microstructure is substantially free of porous voids.

In some embodiments, the additively manufactured aluminum alloy of has a tensile strength of at least 400 MPa. In various embodiments, the additively manufactured aluminum alloy has a tensile strength of about, or at least about, 250, 300, 300, 350, 400, 450, or 500 MPa.

In some embodiments, the additively manufactured aluminum alloy microstructure has a crystallographic texture that is not solely oriented in an additive-manufacturing build direction. For example, the additively manufactured aluminum alloy microstructure may contain a plurality of dendrite layers having differing primary growth-direction angles with respect to each other.

Some variations of the present invention provide an aluminum alloy additive manufacturing process comprising:

(a) obtaining aluminum;

(b) obtaining at least one strengthening element selected from the group consisting of zinc, silicon, copper, magnesium, lithium, silver, titanium, chromium, manganese, iron, vanadium, bismuth, gallium, lead, and combinations thereof;

(c) combining the aluminum with the strengthening element(s), to generate microparticles;

(d) chemically and/or physically disposing at least one grain-refining element on surfaces of the microparticles, to generate functionalized microparticles, wherein the grain-refining element is selected from the group consisting of zirconium, tantalum, niobium, titanium, boron, tungsten, carbon, and oxides, nitrides, hydrides, carbides, borides, or aluminides thereof, and combinations of any of the foregoing; and

(e) additively manufacturing an aluminum alloy from the functionalized microparticles, wherein the resulting additively manufactured aluminum alloy has a microstructure with equated grains.

The additive manufacturing process may be selected from the group consisting of selective laser melting, energy-beam melting, laser engineered net shaping, and combinations thereof, for example.

Selective laser melting (SLM) is an additive manufacturing technique designed to use a high power-density laser to melt and fuse metallic powders together. The SLM process has the ability to fully melt the metal material into a solid 3D part.

Electron-beam melting is a type of additive manufacturing for metal parts. Metal powder is welded together, layer by layer, under vacuum using an electron beam as the heat source.

Laser engineered net shaping is an additive manufacturing technique developed for fabricating metal parts directly from a computer-aided design solid model by using a metal powder injected into a molten pool created by a focused, high-powered laser beam. Laser engineered net shaping is similar to selective laser sintering, but the metal powder is applied only where material is being added to the part at that moment. Note that “net shaping” is meant to encompass “near net” fabrication as well.

In any of these additive manufacturing techniques, post-production processes such as heat treatment, light machining, surface finishing, coloring, stamping, or other finishing operations may be applied. Also, several additive manufactured parts may be joined together chemically or physically to produce a final object.

Functionalized feedstocks for producing aluminum alloys may be powder feedstocks, wire feedstocks, or feedstocks having other geometries. As intended herein, “powder feedstocks” refers to any powdered ceramic, metal, polymer, glass, composite, or combination thereof. In some embodiments, the powder feedstocks are metals or metal-containing compounds. Powder particle sizes are typically between about 1 micron and about 1 mm, but in some cases could be as much as about 1 cm. Wire feedstocks, or feedstocks having other geometries, may be obtained from powders using melting and resolidification, or powder extrusion, for example.

The powdered feedstock may be in any form in which discrete particles can be reasonably distinguished from the bulk. The powder may be present as loose powders, a paste, a suspension, or a green body, for example. A green body is an object whose main constituent is weakly bound powder material, before it has been melted and solidified.

Particles may be solid, hollow, or a combination thereof. Particles can be made by any means including, for example, gas atomization, milling, cryomilling, wire explosion, laser ablation, electrical-discharge machining, or other techniques known in the art. The powder particles may be characterized by an average aspect ratio from about 1:1 to about 100:1. The “aspect ratio” means the ratio of particle length to width, expressed as length:width. A perfect sphere has an aspect ratio of 1:1. For a particle of arbitrary geometry, the length is taken to be the maximum effective diameter and the width is taken to be the minimum effective diameter.

In some embodiments, the particles within the aluminum alloys are rod-shaped particles or domains resembling long sticks, dowels, or needles. The average diameter of the rod-shaped particles or domains may be selected from about 5 nanometers to about 100 microns, for example. Rods need not be perfect cylinders, i.e. the axis is not necessarily straight and the diameter is not necessarily a perfect circle. In the case of geometrically imperfect cylinders (i.e. not exactly a straight axis or a round diameter), the aspect ratio is the actual axial length, along its line of curvature, divided by the effective diameter, which is the diameter of a circle having the same area as the average cross-sectional area of the actual nanorod shape.

The powder material particles may be anisotropic. As meant herein, “anisotropic” particles have at least one chemical or physical property that is directionally dependent. When measured along different axes, an anisotropic particle will have some variation in a measurable property. The property may be physical (e.g., geometrical) or chemical in nature, or both. The property that varies along multiple axes may simply be the presence of mass; for example, a perfect sphere would be geometrically isotropic while a cylinder is geometrically anisotropic. The amount of variation of a chemical or physical property may be 5%, 10%, 20%, 30%, 40%, 50%, 75%, 100% or more.

“Solidification” generally refers to the phase change from a liquid to a solid. In some embodiments, solidification refers to a phase change within the entirety of the powder volume. In other embodiments, solidification refers to a phase change at the surface of the particles or within a fractional volume of the powder material. In various embodiments, at least (by volume) 1%, 2%, 5%, 10%, 15%, 20%, 25%, 30%, 40%, 50%, 60%, 70%, 80%, 90%, 95%, 99%, or 100% of the powdered material is melted to form the liquid state.

For a metal or mixtures of metals, solidification generally results in one or more solid metal phases that are typically crystalline, but sometimes amorphous. Ceramics also may undergo crystalline solidification or amorphous solidification. Metals and ceramics may form an amorphous region coinciding with a crystalline region (e.g., in semicrystalline materials). In the case of certain polymers and glasses, solidification may not result in a crystalline solidification. In the event of formation of an amorphous solid from a liquid, solidification refers to a transition of the liquid from above the glass-transition temperature to an amorphous solid at or below the glass-transition temperature. The glass-transition temperature is not always well-defined, and sometimes is characterized by a range of temperatures.

“Surface functionalization” refers to a surface modification on the powdered materials, which modification significantly affects the solidification behavior (e.g., solidification rate, yield, selectivity, heat release, etc.) of the powder materials. In various embodiments, a powdered material is functionalized with about 1%, 2%, 5%, 10%, 15%, 20%, 25%, 30%, 40%, 50%, 60%, 70%, 80%, 85%, 90%, 95%, 99%, or 100% of the surface area of the powdered material having the surface-functionalization modifications. The surface modification maybe a surface-chemistry modification, a physical surface modification, or a combination thereof.

In some embodiments, the surface functionalization includes a nanoparticle coating and/or a microparticle coating. The nanoparticles and/or microparticles may include a metal, ceramic, polymer, or carbon, or a composite or combination thereof. The surface functionalization may include nanoparticles that are chemically or physically disposed on the surface of the powder materials.

Nanoparticles or microparticles may be attached using electrostatic forces, Van der Waals forces, chemical bonds, mechanical bonds, and/or any other force. A chemical bond is the force that holds atoms together in a molecule or compound. Electrostatic and Van der Waals forces are examples of physical forces that can cause bonding. A mechanical bond is a bond that arises when molecular entities become entangled in space. Typically, chemical bonds are stronger than physical bonds.

The nanoparticles or microparticles are typically a different composition than the base powder. Nanoparticles or microparticles may include metals, hydrides, carbides, nitrides, borides, oxides, intermetallics, or other materials which upon processing form one or more of the aforementioned materials. In some preferred embodiments, nanoparticles are less than 250 nm in average size.

Due to the small size of nanoparticles, benefits may be possible with less than 1% surface area coverage. In the case of functionalization with a nanoparticle of the same composition as the base powder, a surface-chemistry change may not be detectible and can be characterized by topological differences on the surface, for example. Functionalization with a nanoparticle of the same composition as the base powder may be useful to reduce the melting point in order to initiate sintering at a lower temperature, for example.

In some embodiments, microparticles coat micropowders. The micropowder particles may include ceramic, metal, polymer, glass, or combinations thereof. The microparticles (coating) may include metal, ceramic, polymer, carbon, or combinations thereof. In the case of microparticles coating other micropowders, functionalization preferably means that the coating particles are of significantly different dimension(s) than the base powder. For example, the microparticles may be characterized by an average dimension (e.g., diameter) that is less than 20%, 10%, 5%, 2%, or 1% of the largest dimension of the coated powders.

In some embodiments, surface functionalization is in the form of a continuous coating or an intermittent coating. A continuous coating covers at least 90% of the surface, such as about 95%, 99%, or 100% of the surface (recognizing there may be defects, voids, or impurities at the surface). An intermittent coating is non-continuous and covers less than 90%, such as about 80%, 70%, 60%, 50%, 40%, 30%, 20%, 10%, 5%, 2%, 1%, or less of the surface. An intermittent coating may be uniform (e.g., having a certain repeating pattern on the surface) or non-uniform (e.g., random).

In general, the coating may be continuous or discontinuous. The coating may have several characteristic features. In one embodiment, the coating may be smooth and conformal to the underlying surface. In another embodiment, the coating may be nodular. The nodular growth is characteristic of kinetic limitations of nucleation and growth. For example, the coating may look like cauliflower or a small fractal growing from the surface. These features can be affected by the underling materials, the method of coating, reaction conditions, etc.

A coating may or may not be in the form of nanoparticles or microparticles. That is, the coating may be derived from nanoparticles or microparticles, while discrete nanoparticles or microparticles may no longer be present. Various coating techniques may be employed, such as (but not limited to) electroless deposition, immersion deposition, or solution coating. The coating thickness is preferably less than about 20% of the underlying particle diameter, such as less than 15%, 10%, 5%, 2%, or 1% of the underlying particle diameter.

In some embodiments, the surface functionalization also includes direct chemical or physical modification of the surface of the powder materials, such as to enhance the bonding of the nanoparticles or microparticles. Direct chemical modification of the surface of the powder materials, such as addition of molecules, may also be utilized to affect the solidification behavior of the powder materials. A plurality of surface modifications described herein may be used simultaneously.

Nanoparticles are particles with the largest dimension between about 1 nm and 5000 nm. Microparticles are particles with the largest dimension between about 1 micron and 1000 microns. The nanoparticle or microparticle size may be selected based on the desired properties and final function of the assembly.

Nanoparticles or microparticles may be spherical or of arbitrary shape with the largest dimension typically not exceeding the above largest dimensions. An exception is structures with extremely high aspect ratios, such as carbon nanotubes in which the dimensions may include up to 100 microns in length but less than 100 nm in diameter. The nanoparticles or microparticles may include a coating of one or more layers of a different material. Mixtures of nanoparticles and microparticles may be used. In some embodiments, microparticles themselves are coated with nanoparticles, and the microparticle/nanoparticle composite is incorporated as a coating or layer on the powder material particles.

In some embodiments, the nanoparticles and/or microparticles are selected to control solidification of a portion of the powdered material, such as a region of powdered material for which solidification control is desired. Other regions containing conventional powdered materials, without nanoparticles and/or microparticles, may be present. In some embodiments, the nanoparticles and/or microparticles are selected to control solidification of a portion of each the particles (e.g., less than the entire volume of a particle, such as an outer shell).

Various material combinations are possible. In some embodiments, the powder particles are ceramic and the nanoparticles and/or microparticles are ceramic. In some embodiments, the powder particles are ceramic and the nanoparticles and/or microparticles are metallic. In some embodiments, the powder particles are polymeric and the nanoparticles and/or microparticles are metallic, ceramic, or carbon-based. In some embodiments, the powder particles are glass and the nanoparticles and/or microparticles are metallic. In some embodiments, the powder particles are glass and the nanoparticles and/or microparticles are ceramic. In some embodiments, the powder particles are ceramic or glass and the nanoparticles and/or microparticles are polymeric or carbon-based, and so on.

Exemplary ceramic materials for the powders, or the nanoparticles and/or microparticles, include (but are not limited to) SiC, HfC, TaC, ZrC, NbC, WC, TiC, TiC_(0.7)N_(0.3), VC, B₄C, TiB₂, HfB₂, TaB₂, ZrB₂, WB₂, NbB₂, TaN, HfN, BN, ZrN, TiN, NbN, VN, Si₃N₄, Al₂O₃, MgAl₂O₃, HfO₂, ZrO₂, Ta₂O₅, TiO₂, SiO₂, and oxides of rare-earth elements Y, La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and/or Lu.

Exemplary metallic materials for the powders, or the nanoparticles and/or microparticles, include (but are not limited to) Sc, Ti, V, Cr, Y, Zr, Nb, Mo, Ru, Rh, Pd, La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Ta, W, Re, Os, Ir, Pt, Si, or B.

Exemplary polymer materials for the powders, or the nanoparticles and/or microparticles, include (but are not limited to) thermoplastic organic or inorganic polymers, or thermoset organic or inorganic polymers. Polymers may be natural or synthetic.

Exemplary glass materials for the powders include (but are not limited to) silicate glasses, porcelains, glassy carbon, polymer thermoplastics, metallic alloys, ionic liquids in a glassy state, ionic melts, and molecular liquids in a glassy state.

Exemplary carbon or carbon-based materials for the nanoparticles and/or microparticles include (but are not limited to) graphite, activated carbon, graphene, carbon fibers, carbon nanostructures (e.g., carbon nanotubes), and diamond (e.g., nanodiamonds).

These categories of materials are not mutually exclusive; for example a given material may be metallic/ceramic, a ceramic glass, a polymeric glass, etc.

The selection of the coating/powder composition will be dependent on the desired properties and should be considered on a case-by-case basis. Someone skilled in the art of material science or metallurgy will be able to select the appropriate materials for the intended process, based on the information provided in this disclosure. The processing and final product configuration should also be dependent on the desired properties. Someone skilled in the art of material science, metallurgy, and/or mechanical engineering will be able to select the appropriate processing conditions for the desired outcome, based on the information provided in this disclosure.

In some embodiments, a method of controlling solidification of a powdered material comprises:

providing a powdered material comprising a plurality of particles, wherein the particles are fabricated from a first material, and wherein each of the particles has a particle surface area that is surface-functionalized with nanoparticles and/or microparticles;

melting at least a portion of the powdered material to a liquid state; and

semi-passively controlling solidification of the powdered material from the liquid state to a solid state.

As intended in this description, “semi-passive control,” “semi-passively controlling,” and like terminology refer to control of solidification during heating, cooling, or both heating and cooling of the surface-functionalized powder materials, wherein the solidification control is designed prior to melting through selected functionalization and is not actively controlled externally once the melt-solidification process has begun. Note that external interaction is not necessarily avoided. In some embodiments, semi-passive control of solidification further includes selecting the atmosphere (e.g., pressure, humidity, or gas composition), temperature, or thermal input or output. These factors as well as other factors known to someone skilled in the art may or may not be included in semi-passive control.

Exemplary semi-passive control processes, enabled through surface functionalization as described herein, will now be illustrated.

One route to control nucleation is the introduction, into the liquid phase, of nanoparticles derived from a coating described above. The nanoparticles may include any material composition described above and may be selected based on their ability to wet into the melt. Upon melt initiation, the nanoparticles wet into the melt pool as dispersed particles which, upon cooling, serve as nucleation sites, thereby producing a fine-grained structure with observable nucleation sites in the cross-section. In some embodiments, the density of nucleation sites is increased, which may increase the volumetric freezing rate due to the number of growing solidification fronts and the lack of a nucleation energy barrier.

In an exemplary embodiment, ceramic nanoparticles, e.g. TiB₂ or Al₂O₃ nanoparticles, are coated onto aluminum alloy microparticles. The ceramic nanoparticles are introduced into an aluminum alloy melt pool in an additive manufacturing process. The nanoparticles then disperse in the melt pool and act as nucleation sites for the solid. The additional well-dispersed nucleation sites can mitigate shrinkage cracks (hot cracking). Shrinkage cracks typically occur when liquid cannot reach certain regions due to blockage of narrow channels between solidifying grains. An increase in nucleation sites can prevent formation of long, narrow channels between solidifying grains, because multiple small grains are growing, instead of few large grains.

In another exemplary embodiment, nanoparticles act as nucleation sites for a secondary phase in an alloy. The nanoparticles may comprise the secondary phase or a material that nucleates the secondary phase (due to similar crystal structures, for instance). This embodiment can be beneficial if the secondary phase is responsible for blocking interdendritic channels leading to hot cracking. By nucleating many small grains of the secondary phase, a large grain that might block the narrow channel between the dendrites can be avoided. Furthermore, this embodiment can be beneficial if the secondary phase tends to form a continuous phase between the grains of the primary phase, which promotes stress corrosion cracking. By providing additional nucleation sites for the secondary phase, this secondary phase may be broken up and interdispersed, preventing it from forming a continuous phase between grains of the primary alloy. By breaking up a secondary phase during solidification, there is the potential to more completely homogenize the material during heat treatment, which can decrease the likelihood of stress corrosion cracking (fewer gradients in the homogenized material). If the secondary phase is not continuous, long notches from corrosion are less likely.

In another embodiment of nucleation control, the functionalized surface may fully or partially dissolve in the melt and undergo a reaction with materials in the melt to form precipitates or inclusions, which may act in the same manner as the nanoparticles in the preceding paragraph. For example, titanium particles may be coated on an aluminum alloy particle, which upon melting would dissolve the titanium. However, on cooling the material undergoes a reaction, forming aluminum-titanium intermetallic (Al₃Ti) inclusions which would serve as nucleation sites.

In another embodiment, the coating may react with impurities to form nucleation sites. An example is a magnesium coating on a titanium alloy powder. Titanium has a very high solubility of oxygen (a common atmospheric contaminant), which can affect the overall properties. A coating of magnesium reacts within the melt, binding to dissolved oxygen which forms magnesium oxide (MgO) inclusions, promoting nucleation.

Nucleation control may include the use of ceramic particles. In some embodiments, the ceramic particles can be wet by the molten material, while in other embodiments, the ceramic particles cannot be wet by the molten material. The ceramic particles may be miscible or immiscible with the molten state. The ceramic particles may be incorporated into the final solid material. In some embodiments, the ceramic particles are rejected from the solid. Exemplary ceramic materials include (but are not limited to) SiC, HfC, TaC, ZrC, NbC, WC, TiC, TiC_(0.7)N_(0.3), VC, B₄C, TiB₂, HfB₂, TaB₂, ZrB₂, WB₂, NbB₂, TaN, HfN, BN, ZrN, TiN, NbN, VN, Si₃N₄, Al₂O₃, MgAl₂O₃, HfO₂, ZrO₂, Ta₂O₅, TiO₂, SiO₂, and oxides of rare-earth elements Y, La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and/or Lu.

Nucleation control may include the use of metallic particles. In some embodiments, the metallic particles can be wet by the molten material. The metallic particles may form an alloy with the molten material through a eutectic reaction or peritectic reaction. The alloy may be an intermetallic compound or a solid solution. In some embodiments, the metallic particles cannot be wet by the molten material and cannot form an alloy with the molten material. Exemplary metallic materials include (but are not limited to) Sc, Ti, V, Cr, Y, Zr, Nb, Mo, Ru, Rh, Pd, La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Ta, W, Re, Os, Ir, Pt, Si, or B.

Nanoparticles promote surface growth of crystals that have good epitaxial fit. Nucleation on the surface of a nanoparticle is more likely when there is good fit between the crystal lattice parameters of the nanoparticles and the solidifying material. Nanoparticles may be selected to promote nucleation of a specific phase in the melt.

Generally, nucleation-promoting chemical reactions are dependent on the selected surface functionalization and on the heating (or cooling) parameters.

As nanoparticles or microparticles are organized on a particle surface under conditions for which rapid melting or near melting occurs and rapidly fuses the particles together with very little melt convection, the coating will not have the time or associated energy to diffuse away from its initial position relative to the other powders. This would in turn create a three-dimensional network structure of inclusions. Thus, a method is provided to control maximum grain size and/or to design a predictable microstructure. The microstructure is dependent on the initial powder size, shape, and packing configuration/density. Adjusting the coating and powder parameters allows control of this hierarchical structure. In some embodiments, these architectures significantly improve material properties by impeding, blocking, or redirecting dislocation motion in specific directions, thereby reducing or eliminating failure mechanisms.

Utilizing the appropriate functionalization, the heat flow during solidification may be controlled using heats of fusion or vaporization. In some embodiments, inclusions are pulled into the melt or reacted within the melt (as described above). In some embodiments, a coating is rejected to the surface of the melt pool. Utilizing a functionalization surface with a high vapor pressure at the desired melting point of the powder, vaporization would occur, resulting in a cooling effect in the melt which increases the freezing rate. As described above, magnesium on a titanium alloy may accomplish this, in addition to forming oxide inclusions. The effect of this is detectible when comparing non-functionalized powders to functionalized powders under identical conditions, as well as comparing the composition of feed material versus the composition of the final product.

In another embodiment, the opposite effect occurs. Some systems may require slower solidification times than can be reasonably provided in a certain production system. In this instance, a higher-melting-point material, which may for example be rejected to the surface, freezes. This releases the heat of fusion into the system, slowing the total heat flux out of the melt. Heat may also be held in the melt to slow solidification by incorporating a secondary material with a significantly higher heat capacity.

In another embodiment, the heat of formation is used to control heat flow during melt pool formation and/or solidification. For example, nickel microparticles may be decorated with aluminum nanoparticles. Upon supply of enough activation energy, the exothermic reaction of Ni and Al to NiAl is triggered. In this case, a large heat of formation is released (−62 kJ/mol) which may aid in melting the particles fully or partially. The resulting NiAl intermetallic is absorbed into the melt and stays suspended as a solid (a portion may be dissolved) due to its higher melting point, thereby acting as a nucleation site as well as having a strengthening effect on the alloy later.

Thermodynamic control of solidification may utilize nanoparticle or microparticle surface coatings which undergo a phase transformation that is different from phase transformations in the base material. The phase transformations may occur at different solidus and/or liquidus temperatures, at similar solidus and/or liquidus temperatures, or at the same solidus and/or liquidus temperatures. The phase-transformed nanoparticles/microparticles or surface coatings may be incorporated into the final solid material, or may be rejected from the final solid material, or both of these. The phase-transformed nanoparticles/microparticles or surface coatings may be miscible or immiscible with the molten state. The phase-transformed nanoparticles/microparticles or surface coatings may be miscible or immiscible with the solid state.

Thermodynamic control of solidification may utilize nanoparticles/microparticles or surface coatings which vaporize or partially vaporize. For example, such coatings may comprise organic materials (e.g., waxes, carboxylic acids, etc.) or inorganic salts (e.g., MgBr₂, ZnBr₂, etc.).

Thermodynamic control of solidification may utilize nanoparticles/microparticles or surface coatings which release or absorb gas (e.g., oxygen, hydrogen, carbon dioxide, etc.).

Thermodynamic control of solidification may utilize nanoparticle or microparticle surface coatings with different heat capacities than the base material.

In addition to controlling the energy within the system, it also is possible to control the rate at which heat leaves the system by controlling thermal conductivity or emissivity (thermal IR radiation). This type of control may be derived from a rejection to the surface or from the thermal conductivity of a powder bed during additive manufacturing, for instance. In one embodiment, the functionalization may reject to the surface a low-conductivity material, which may be the functionalization material directly or a reaction product thereof, which insulates the underlying melt and decreases the freezing rate. In other embodiments, a layer may have a high/low emissivity which would increase/decrease the radiative heat flow into or out of the system. These embodiments are particularly applicable in electron-beam systems which are under vacuum and therefore radiation is a primary heat-flow mechanism.

Additionally, in laser sintering systems, the emissivity of a rejected layer may be used to control the amount of energy input to the powder bed for a given wavelength of laser radiation. In another embodiment, the functionalized surface may be fully absorbed in the melt yet the proximity to other non-melted functionalized powders, such as additive manufacturing in a powder bed, may change the heat conduction out of the system. This may manifest itself as a low-thermal-conductivity base powder with a high-conductivity coating.

Thermal conductivity or emissivity control of solidification may utilize nanoparticle or microparticle surface coatings which are higher in thermal conductivity compared to the base material. The nanoparticle or microparticle surface coatings may be incorporated into the melt, or may be rejected, such as to grain boundaries or to the surface of the melt. The nanoparticle or microparticle surface coatings may be miscible or immiscible with the molten state and/or with the final solid state.

Thermal conductivity or emissivity control of solidification may utilize nanoparticle or microparticle surface coatings which are lower in thermal conductivity compared to the base material.

Thermal conductivity or emissivity control of solidification may utilize nanoparticle or microparticle surface coatings which are higher in emissivity compared to the base material.

Thermal conductivity or emissivity control of solidification may utilize nanoparticle or microparticle surface coatings which are lower in emissivity compared to the base material.

In some embodiments, the functionalization material may react with contaminants in the melt (e.g., Mg—Ti—O system). When the functionalization material is properly chosen, the reacted material may be selected such that the formed reaction product has a high surface tension with the liquid, such that it may be rejected to the surface. The rejected reaction product may take the form of an easily removable scale. Optionally, the rejected layer is not actually removed but rather incorporated into the final product. The rejected layer may manifest itself as a hard-facing carbide, nitride, or oxide coating, a soft anti-galling material, or any other functional surface which may improve the desired properties of the produced material. In some cases, the rejected surface layer may be of a composition and undergo a cooling regime which may result in an amorphous layer on the surface of the solidified material. These surface-rejected structures may result in improved properties related to, but not limited to, improved corrosion resistance, stress corrosion crack resistance, crack initiation resistance, overall strength, wear resistance, emissivity, reflectivity, and magnetic susceptibility.

Through contaminant removal or rejection, several scenarios are possible. Nanoparticles/microparticles or surface coatings that react with or bind to undesired contaminants may be incorporated into the solidification, in the same phase or a separate solid phase. The reacted nanoparticle or microparticle surface coatings may be rejected during solidification. When portions or select elements present in the nanoparticle or microparticle surface coatings react with or bind to contaminants, such portions or elements may be incorporated and/or rejected.

In some embodiments, the functionalized surface reacts upon heating to form a lower-melting-point material compared to the base material, such as through a eutectic reaction. The functionalized surface may be chosen from a material which reacts with the underlying powder to initiate melting at the particle surface, or within a partial volume of the underlying powder. A heat source, such as a laser or electron beam, may be chosen such that the energy density is high enough to initiate the surface reaction and not fully melt the entire functionalized powder. This results in an induced uniform liquid phase sintering at the particle surface. Upon freezing, the structure possesses a characteristic microstructure indicating different compositions and grain nucleation patterns around a central core of stock powder with a microstructure similar to the stock powder after undergoing a similar heat treatment. This structure may later be normalized or undergo post-processing to increase density or improve the properties.

In some embodiments, a reaction occurs in which one component melts and this melted material diffuses into a second nanoparticle or microparticle, to form an alloyed solid. This new alloyed solid may then act as a phase-nucleation center, or may limit melting just at the edge of particles.

Incorporating nanoparticles into a molten metal may be challenging when the nanoparticles have a thin oxide layer at the surface, since liquid metals typically do not wet oxides well. This may cause the nanoparticles to get pushed to the surface of the melt. One way to overcome the oxide layer on nanoparticles, and the associated wettability issues, is to form the nanoparticles in situ during melt pool formation. This may be achieved by starting with nanoparticles of an element that forms an intermetallic with one component of the base alloy, while avoiding dissolution of the nanoparticles in the melt. Alternatively, binary compound nanoparticles that disassociate at elevated temperatures, such as hydrides or nitrides, may be used since the disassociation reaction annihilates any oxide shell on the nanoparticle.

As noted above, the surface functionalization may be designed to be reacted and rejected to the surface of the melt pool. In embodiments employing additive manufacturing, layered structures may be designed. In some embodiments, progressive build layers and hatchings may be heated such that each sequential melt pool is heated long enough to reject the subsequent rejected layer, thereby producing a build with an external scale and little to no observable layering within the build of the rejected materials. In other embodiments, particularly those which result in a functional or desired material rejected to the surface, heating and hatching procedures may be employed to generate a composite structure with a layered final product. Depending on the build parameters, these may be randomly oriented or designed, layered structures which may be used to produce materials with significantly improved properties.

Architected microstructures may be designed in which feature sizes (e.g., distance between nanoparticle nodes) within the three-dimensional network are selected, along with targeted compositions, for an intended purpose. Similarly, layered composite structures may be designed in which feature sizes (e.g., layer thicknesses or distance between layers) are selected, along with targeted compositions, for an intended purpose.

Note that rejection to the surface is not necessarily required to generate layered structures. Functionalized surfaces may be relatively immobile from their initial position on the surface of the base powder. During melting, these functionalized surfaces may act as nucleation sites, as previously mentioned; however, instead of absorption into the melt, they may initiate nucleation at the location which was previously occupied by the powder surface and is not molten. The result is a fine-grained structure evolving from the surface nucleation source, towards the center. This may result in a designed composite structure with enhanced properties over the base material. In general, this mechanism allows for the ability to control the location of desired inclusions through controlled solidification.

In the additive manufacturing of titanium alloys, the problem of microstructural texturing of subsequent layers of molten metals induces anisotropic microstructures and thus anisotropic structural properties. Dispersing stable ceramic nanoparticles in the solidifying layers may produce grain structures with isotropic features which are stable upon repetitive heating cycles. An example is a stable high-temperature ceramic nanoparticle, such as Al₂O₃ or TiCN attached to the surface of a Ti-6Al-4V microparticle powder which is subsequently melted, solidified, and then reheated as the next layer of powder is melted on top. The ceramic nanoparticles can induce nucleation of small grains and prevent coarse grains from forming in the direction of the thermal gradient.

In some embodiments, the solid state of an aluminum alloys is a three-dimensional microstructure containing the nanoparticles and/or microparticles as inclusions distributed throughout the solid state. In some embodiments, the solid state of an aluminum alloys is a layered microstructure containing one or more layers comprising the nanoparticles and/or microparticles.

The method may further include creating a structure through one or more techniques selected from the group consisting of additive manufacturing, injection molding, pressing and sintering, capacitive discharge sintering, and spark plasma sintering. The present invention provides a solid object or article, as an aluminum alloy, comprising a structure produced using such a method.

Some variations provide an aluminum alloy created from the functionalized powder via additive manufacturing. The functionalized powder (with nanoparticle or microparticle surface coating) may be incorporated into the final structure. In some embodiments, the nanoparticle or microparticle surface coating is rejected, creating a scale. The scale may be unbonded to the structure. In some embodiments, the scale bonds to the structure or otherwise cannot be readily removed. This may be advantageous, such as to provide a structural enhancement—for instance, rejected ceramic particles may add a hard facing to the final structure. A rejected nanoparticle or microparticle surface coating may form a multilayer composite, wherein each layer has a different composition. In some embodiments, a rejected nanoparticle or microparticle surface coating forms a spatially graded composition within the bulk of the structure. A three-dimensional architecture may also develop in the final microstructure.

Some variations provide a solid aluminum alloy object or article comprising at least one solid phase (i) containing a powdered material as described, or (ii) derived from a liquid form of a powdered material as described. The solid phase may form from 0.25 wt % to 100 wt % of the solid object or article, such as about 1 wt %, 5 wt %, 10 wt %, 25 wt %, 50 wt %, or 75 wt % of the solid object or article, for example.

Other variations provide a solid aluminum alloy object or article comprising a continuous solid phase and a three-dimensional network of nanoparticle and/or microparticle inclusions distributed throughout the continuous solid phase, wherein the three-dimensional network blocks, impedes, or redirects dislocation motion within the aluminum alloy object or article.

In some embodiments, nanoparticle and/or microparticle inclusions are distributed uniformly throughout the continuous solid phase of the aluminum alloy. The nanoparticle and/or microparticle inclusions may be present at a concentration from about 0.1 wt % to about 50 wt % of the solid object or article, such as about 1, 2, 5, 10, 15, 20, 25, 30, 35, 40, or 45 wt %, for example.

In some embodiments, light elements are incorporated into the aluminum alloy or into a final object incorporating the aluminum alloy. For example, the particle surface (or the surface of nanoparticles or microparticles present on the powder particles) may be surface-reacted with an element selected from the group consisting of hydrogen, oxygen, carbon, nitrogen, boron, sulfur, and combinations thereof, or essentially any other element(s) as desired. For example, reaction with hydrogen gas may be carried out to form a metal hydride. Optionally, the particle or a particle coating further contains a salt, carbon, an organic additive, an inorganic additive, or a combination thereof. Certain embodiments utilize relatively inert carbides that are incorporated (such as into steel) with fast melting and solidification.

Methods of producing surface-functionalized powder materials are generally not limited and may include immersion deposition, electroless deposition, vapor coating, solution/suspension coating of particles with or without organic ligands, utilizing electrostatic forces and/or Van der Waals forces to attach particles through mixing, and so on. U.S. patent application Ser. No. 14/720,757 (filed May 23, 2015), U.S. patent application Ser. No. 14/720,756 (filed May 23, 2015), and U.S. patent application Ser. No. 14/860,332 (filed Sep. 21, 2015), each commonly owned with the assignee of this patent application, are hereby incorporated by reference herein. These disclosures relate to methods of coating certain materials onto micropowders, in some embodiments.

For example, as described in U.S. patent application Ser. No. 14/860,332, coatings may be applied using immersion deposition in an ionic liquid, depositing a more-noble metal on a substrate of a less-noble, more-electronegative metal by chemical replacement from a solution of a metallic salt of the coating metal. This method requires no external electric field or additional reducing agent, as with standard electroplating or electroless deposition, respectively. The metals may be selected from the group consisting of aluminum, zirconium, titanium, zinc, nickel, cobalt copper, silver, gold, palladium, platinum, rhodium, titanium, molybdenum, uranium, niobium, tungsten, tin, lead, tantalum, chromium, iron, indium, rhenium, ruthenium, osmium, iridium, and combinations or alloys thereof.

Organic ligands may be reacted onto a metal, in some embodiments. Organic ligands may be selected from the group consisting of aldehydes, alkanes, alkenes, silicones, polyols, poly(acrylic acid), poly(quaternary ammonium salts), poly(alkyl amines), poly(alkyl carboxylic acids) including copolymers of maleic anhydride or itaconic acid, poly(ethylene imine), poly(propylene imine), poly(vinylimidazoline), poly(trialkylvinyl benzyl ammonium salt), poly(carboxymethylcellulose), poly(D- or L-lysine), poly(L-glutamic acid), poly(L-aspartic acid), poly(glutamic acid), heparin, dextran sulfate, 1-carrageenan, pentosan polysulfate, mannan sulfate, chondroitin sulfate, and combinations or derivatives thereof.

The reactive metal may be selected from the group consisting of alkali metals, alkaline earth metals, aluminum, silicon, titanium, zirconium, hafnium, zinc, and combinations or alloys thereof. In some embodiments, the reactive metal is selected from aluminum, magnesium, or an alloy containing greater than 50 at % of aluminum and/or magnesium.

Some possible powder metallurgy processing techniques that may be used include, but are not limited to, hot pressing, low-pressure sintering, extrusion, metal injection molding, and additive manufacturing.

The final article (the aluminum alloy or a part containing such alloy) may have porosity from 0% to about 75%, such as about 5%, 10%, 20%, 30%, 40%, 50%, 60%, or 70%, in various embodiments. The porosity may derive from space both within particles (e.g., hollow shapes) as well as space outside and between particles. The total porosity accounts for both sources of porosity.

The final aluminum alloy may be selected from the group consisting of a sintered structure, a coating, a geometric object, a billet, an ingot, a net-shape part, a near-net-shape part, and combinations thereof. The article may be produced from the coated reactive metal by a process comprising one or more techniques selected from the group consisting of hot pressing, cold pressing, sintering, extrusion, injection molding, additive manufacturing, electron-beam melting, selective laser sintering, pressureless sintering, and combinations thereof.

In some embodiments of the invention, the coated particles are fused together to form a continuous or semi-continuous material. As intended in this specification, “fused” should be interpreted broadly to mean any manner in which particles are bonded, joined, coalesced, or otherwise combined, at least in part, together. Many known techniques may be employed for fusing together particles.

In various embodiments, fusing is accomplished by sintering, heat treatment, pressure treatment, combined heat/pressure treatment, electrical treatment, electromagnetic treatment, melting/solidifying, contact (cold) welding, solution combustion synthesis, self-propagating high-temperature synthesis, solid state metathesis, or a combination thereof.

“Sintering” should be broadly construed to mean a method of forming a solid mass of material by heat and/or pressure without melting the entire mass to the point of liquefaction. The atoms in the materials diffuse across the boundaries of the particles, fusing the particles together and creating one solid piece. The sintering temperature is typically less than the melting point of the material. In some embodiments, liquid-state sintering is used, in which some but not all of the volume is in a liquid state.

When sintering or another heat treatment is utilized, the heat or energy may be provided by electrical current, electromagnetic energy, chemical reactions (including formation of ionic or covalent bonds), electrochemical reactions, pressure, or combinations thereof. Heat may be provided for initiating chemical reactions (e.g., to overcome activation energy), for enhancing reaction kinetics, for shifting reaction equilibrium states, or for adjusting reaction network distribution states.

A sintering technique may be selected from the group consisting of radiant heating, induction, spark plasma sintering, microwave heating, capacitor discharge sintering, and combinations thereof. Sintering may be conducted in the presence of a gas, such as air or an inert gas (e.g., Ar, N₂, He, or CO₂), or in a reducing atmosphere (e.g., H₂ or CO). Various sintering temperatures or ranges of temperatures may be employed. A sintering temperature may be about, or less than about, 100° C., 200° C., 300° C., 400° C., 500° C., 600° C., 700° C., 800° C., 900° C., or 1000° C. A sintering temperature is preferably less than the reactive-metal melting temperature. In some embodiments, a sintering temperature may be less than a maximum alloy melting temperature, and further may be less than a minimum alloy melting temperature. In certain embodiments, the sintering temperature may be within the range of melting points for a selected alloy. In some embodiments, a sintering temperature may be less than a eutectic melting temperature of the particle alloy.

At a peritectic decomposition temperature, rather than melting, a metal alloy decomposes into another solid compound and a liquid. In some embodiments, a sintering temperature may be less than a peritectic decomposition temperature of the metal alloy. If there are multiple eutectic melting or peritectic decomposition temperatures, a sintering temperature may be less than all of these critical temperatures, in some embodiments.

In some embodiments pertaining to aluminum alloys employed in the microparticles, the sintering temperature is preferably selected to be less than about 450° C., 460° C., 470° C., 480° C., 490° C., or 500° C. The decomposition temperature of eutectic aluminum alloys is typically in the range of 400-600° C. (Belov et al., Multicomponent Phase Diagrams: Applications for Commercial Aluminum Alloys, Elsevier, 2005), which is hereby incorporated by reference herein.

Some variations produce or employ metal matrix nanocomposites as part of, or all of, an aluminum alloy. A “metal matrix nanocomposite” is a metal-containing material with greater than 0.1 wt % nanoparticles distributed in a metal matrix or otherwise within the metal-containing material.

Some embodiments produce or employ a functionally graded metal matrix nanocomposite, as part of, or all of, an aluminum alloy. As intended herein, a “functionally graded metal matrix nanocomposite” is a metal matrix nanocomposite that exhibits a spatial gradient of one or more properties, derived from some spatial variation, within the metal matrix, of a nanoparticle or nanoparticle phase. The property that varies may be mechanical, thermal, electrical, photonic, magnetic, or any other type of functional property.

Nanocomposites have been shown to exhibit enhanced mechanical strength due to the ability to impede dislocation motion. This ability is not limited to room temperature and can improve a material's high-temperature strength and creep resistance. Nanocomposites can also improve wear and fouling resistance in certain sliding and high-friction environments.

Metal matrix nanocomposites may be produced with arbitrary composition and with control of nanoparticle volume fraction. Starting with functionalized feedstocks as described above, a low or high volume fraction of nanoparticles may be achieved. There may be a uniform or non-uniform distribution of nanoparticles within the matrix, by utilizing conventional, low-cost powder metallurgy approaches and ingot processing.

Some variations provide a metal matrix nanocomposite composition comprising metal-containing microparticles and nanoparticles, wherein the nanoparticles are chemically and/or physically disposed on surfaces of the microparticles, and wherein the nanoparticles are consolidated in a three-dimensional architecture throughout the composition.

A “three-dimensional architecture” means that the nanoparticles are not randomly distributed throughout the metal matrix nanocomposite. Rather, in a three-dimensional architecture of nanoparticles, there is some regularity in spacing between nanoparticles, in space (three dimensions). The average spacing between nanoparticles may vary, such as from about 1 nanoparticle diameter to about 100 nanoparticle diameters or more, depending on the nanoparticle concentration in the material.

In some embodiments, the three-dimensional architecture of nanoparticles in the metal matrix nanocomposite is correlated to the distribution of nanoparticles within the starting composition (functional microparticles, i.e. metal-containing microparticles with nanoparticles on surfaces). Such a three-dimensional architecture of nanoparticles is possible when the kinetics during melting and solidification are controlled such that the integrity and dispersion of nanoparticles are preserved.

In some embodiments, the nanoparticles do not melt and do not significantly disperse from the original dispositions, relative to each other, following melting of the metal matrix and then during solidification. In certain embodiments, the nanoparticles melt, soften (such as to become a glass), or form a liquid-solution solution, yet do not significantly disperse from the original dispositions, relative to each other, following melting of the metal matrix and/or during solidification. When such nanoparticles resolidify (or undergo a phase transition) during solidification of the melt, they assume their original dispositions or approximate coordinates thereof. In some embodiments, whether or not the nanoparticles melt, the nanoparticles end up in a three-dimensional architecture in which the locations of nanoparticles are different than the original dispositions, but may be correlated and therefore predictable based on the starting functionalized feedstock.

In some embodiments, the composition is an ingot for producing a metal matrix nanocomposite. In other embodiments, the composition itself is a metal matrix nanocomposite.

In some embodiments, an ingot is made or obtained, for later producing a metal matrix nanocomposite. An “ingot” or equivalently “pre-dispersed ingot” means a raw material that contains both a metal component and a pre-dispersed reinforcing nanoparticle component. An ingot may be obtained after processing of a functionalized powder, or after processing of a metal matrix nanocomposite. In some embodiments, the ingot already contains a functional gradient of nanoparticle density. In some embodiments, the ingot has or contains a microstructure indicative of a material which consisted of powder precursors with nanoparticle surface functionalization. This will result in a 3D network of nanoparticles in the ingot.

An ingot may be a green body or a finished body. Ingot relative densities may range from 10% to 100%, for example, calculated as a percentage of the theoretical density (void-free) of the components contained in the ingot.

The use of the ingot may vary. Further processing may result in the redistribution of nanoparticles throughout the structure. The ingot may be processed in such a way that it has the distinct advantage of containing a targeted volume fraction of nanoparticles determined during functionalization and a uniform distribution due to the discrete nanoparticle assembly on the surface of the metal-containing microparticles.

The microparticles may contain an element selected from the group consisting of Al, Mg, Ni, Fe, Cu, Ti, V, Si, and combinations thereof, for example. The nanoparticles may contain a compound selected from the group consisting of metals, ceramics, cermets, intermetallic alloys, oxides, carbides, nitrides, borides, polymers, carbon, and combinations thereof, for example. In certain embodiments, the microparticles contain Al, Si, and Mg (e.g., alloy AlSi10Mg), and the nanoparticles contain tungsten carbide (WC).

Some variations provide a method of making a metal matrix nanocomposite, the method comprising:

(a) providing a precursor composition comprising metal-containing microparticles and nanoparticles, wherein the nanoparticles are chemically and/or physically disposed on surfaces of the microparticles;

(b) consolidating the precursor composition into an intermediate composition comprising the metal-containing microparticles and the nanoparticles, wherein the nanoparticles are consolidated in a three-dimensional architecture throughout the intermediate composition; and

(c) processing the intermediate composition to convert the intermediate composition into a metal matrix nanocomposite.

In some embodiments, the precursor composition is in powder form. In some embodiments, the intermediate composition is in ingot form.

The microparticles may contain an element selected from the group consisting of Al, Mg, Ni, Fe, Cu, Ti, V, Si, and combinations thereof. The nanoparticles may contain a compound selected from the group consisting of metals, ceramics, cermets, intermetallic alloys, oxides, carbides, nitrides, borides, polymers, carbon, and combinations thereof. Typically, the compositions of the microparticles and nanoparticles are different, although it is possible for the chemical composition to be the same or similar while there are differences in physical properties (particle size, phases, etc.).

The composition may contain from about 10 wt % to about 99.9 wt % of microparticles. In these or other embodiments, the composition contains from about 0.1 wt % to about 10 wt % of nanoparticles. Higher concentrations of nanoparticles are possible, particularly when regions with lower concentration are physically removed (as discussed later). A metal matrix nanocomposite may be identified as a “cermet” when metal content is low, such as 20 wt % or less.

In some embodiments, at least 1% of the surface area of the microparticles contains nanoparticles that are chemically and/or physically disposed on the microparticle surfaces. When higher nanoparticle concentrations are desired in the final material, it is preferred that a higher surface area of the microparticles contains nanoparticles. In various embodiments, at least 1%, 2%, 5%, 10%, 20%, 30%, 40%, 50%, 60%, 70%, 80%, 90%, or 95% of the total surface area of the microparticles contains nanoparticles that are chemically and/or physically disposed on the microparticle surfaces.

In some embodiments, the microparticles have an average microparticle size from about 1 micron to about 1 centimeter. In various embodiments, the average microparticle size is about 5 microns, 10 microns, 50 microns, 100 microns, 200 microns, 500 microns, 1 millimeter, 5 millimeters, or 10 millimeters.

In some embodiments, the nanoparticles have an average nanoparticle size from about 1 nanometer to about 5000 nanometers. A preferred size of nanoparticles is about 2000 nm or less, about 1500 nm or less, or about 1000 nm or less. In some embodiments, nanoparticles are at least 50 nm in size. In various embodiments, the average nanoparticle size is about 10, 50, 100, 200, 300, 400, 500, 600, 700, 800, 900, 1000, 1500, 2000, 2500, 3000, or 4000 nanometers.

In some embodiments, the metal matrix has a density from about 2 g/cm³ to about 10 g/cm³. In some embodiments, the nanoparticles independently have a density from about 1 g/cm³ to about 20 g/cm³.

In various embodiments, consolidating includes pressing, binding, sintering, or a combination thereof. Consolidating may alternatively or additionally include metal injection molding, extruding, isostatic pressing, powder forging, spray forming, metal additive manufacturing, and/or other known techniques. The intermediate composition produced by step (b) may be referred to as a green body.

In various embodiments, processing includes pressing, sintering, mixing, dispersing, friction stir welding, extrusion, binding (such as with a polymer binder), melting, semi-solid melting, sintering, casting, or a combination thereof. Melting may include induction melting, resistive melting, skull melting, arc melting, laser melting, electron beam melting, semi-solid melting, or other types of melting (including convention and non-conventional melt processing techniques). Casting may include centrifugal, pour, or gravity casting, for example. Sintering may include spark discharge, capacitive-discharge, resistive, or furnace sintering, for example. Mixing may include convection, diffusion, shear mixing, or ultrasonic mixing, for example.

Steps (b) and (c) collectively convert the precursor composition (e.g., the functionalized powder) into a green body or a finished body which may then be used for additional post processing, machined to a part, or other uses.

In some embodiments, the metal-matrix phase and the first reinforcement phase are each dispersed throughout the nanocomposite. In these or other embodiments, the metal-matrix phase and the first reinforcement phase are disposed in a layered configuration within the nanocomposite, wherein the layered configuration includes at least a first layer comprising the nanoparticles and at least a second layer comprising the metal-matrix phase.

The final metal matrix nanocomposite may have a cast microstructure, in some embodiments. By a “cast microstructure” it is meant that the metal matrix nanocomposite is characterized by a plurality of dendrites and grain boundaries within the microstructure. In some embodiments, there is also a plurality of voids, but preferably no cracks or large phase boundaries. A dendrite is a characteristic tree-like structure of crystals produced by faster growth of crystals along energetically favorable crystallographic directions as molten metal freezes.

Note that while casting is a metal processing technique, a cast microstructure is a structural feature, not necessarily tied to any particular process to make the microstructure. A cast microstructure can certainly result from freezing (solidification) of molten metal or metal alloy. However, metal solidification can result in other microstructures, and cast microstructures can arise from other metal-forming techniques. Metal processes that do not rely at all on melting and solidification (e.g., forming processes) will not tend to produce a cast microstructure.

A cast microstructure can generally be characterized by primary dendrite spacing, secondary dendrite spacing, dendritic chemical segregation profile, grain size, shrinkage porosity (if any), percent of secondary phases, composition of secondary phases, and dendritic/equated transition, for example.

In some embodiments of the present invention, a cast microstructure is further characterized by an equated, fine-grained microstructure. “Equiaxed” grains means that the grains are roughly equal in length, width, and height. Equiaxed grains can result when there are many nucleation sites arising from the plurality of nanoparticles contained on surfaces of microparticles, in the functionalized metal feedstock and therefore in the final metal matrix nanocomposite.

In some embodiments, a cast microstructure is further characterized by a dispersed microstructure. A dispersed microstructure generally arises from the large number of dendrites and grain boundaries within the microstructure, which in turn arise from the large number of nanoparticles on surfaces of microparticles. The degree of dispersion may be characterized by a dispersion length scale, calculated as the average spacing between nanoparticles and/or the average length scale in the metal phase between nanoparticles. In various embodiments, the dispersion length scale is from about 1 nanometer to about 100 microns, such as from about 10 nanometers to about 10 microns, or about 100 nanometers to about 1 micron.

Optionally, porosity may be removed or reduced in a cast microstructure. For example, a secondary heat and/or pressure (or other mechanical force) treatment may be done to minimize porous voids present in the metal matrix nanocomposite. Also, pores may be removed from the metal matrix nanocomposite by physically removing (e.g., cutting away) a region into which porous voids have segregated, such as via density-driven phase segregation.

In addition to removal of voids, other post-working may be carried out, potentially resulting in other final microstructures that are not cast microstructures, or that contain a mixture of microstructures. For example, forging can refine defects from cast ingots or continuous cast bar, and can introduce additional directional strength, if desired. Preworking (e.g., strain hardening) can be done such as to produce a grain flow oriented in directions requiring maximum strength. The final microstructure therefore may be a forged microstructure, or a mixed cast/forged microstructure, in certain embodiments. In various embodiments, the metal matrix microstructure, on a volume basis, is at least 10%, 25%, 50%, 75%, 90%, 95%, 99%, or 100% cast microstructure.

Some variations of the present invention provide a raw material produced by a consolidation method of functionalized powder, to produce an ingot which may be used to make a nanocomposite, or is itself a nanocomposite. The metal alloys and nanoparticle compositions may vary widely, as described elsewhere. Metal matrix nanocomposites herein may be fabricated via compositional-bias assembly, density-bias assembly, hierarchical-size assembly, or other types of assembly of nanoparticles. The nanoparticles may stay the same composition upon ingot formation, the nanoparticles may react in some way to form a more favorable material for the nanocomposite, multiple different nanoparticles may be used, or any combination of this could occur.

Some embodiments produce a master aluminum alloy. A “master alloy” is well-defined in the art and refers to a concentrated alloy source which can be added to a metal being processed, to introduce the appropriate alloying elements into the system. Master alloys are particularly useful when the alloying elements are difficult to disperse or in low weight quantities. In the case of the dispersion difficulties, pre-dispersed master alloys increase wetting and avoid agglomeration. In the case of low quantities, it is much easier to control additions when heavier weights of pre-alloyed material can be added, to avoid weighing errors for the minor alloying elements.

In some variations, a functionally graded metal matrix nanocomposite is fabricated, followed by removal of one or more phases not containing nanoparticles (or containing a lower concentration of nanoparticles) from the nanocomposite, to generate a master alloy metal matrix nanocomposite. The production of a master alloy metal matrix nanocomposite allows for a high volume loading of reinforcement phases into metal matrices. By consolidating a homogenously dispersed nanoparticle reinforcement phase, such as via density-driven phase separation, and then removing a portion that does not contain the nanoparticle reinforcement phase, a master alloy is obtained. The master alloy may be used in further processing to produce a final geometrical configuration, such as in melt processing and casting.

These methods provide low-cost, high-volume production of master alloy metal matrix nanocomposites with high volume loading of nanoparticulate reinforcement. Reaction times may be minimized by using a pre-dispersed metal matrix nanocomposite feedstock powder or feedstock ingot.

Some variations provide a method of making a master alloy metal matrix nanocomposite, the method comprising:

(a) providing an ingot composition comprising metal-containing microparticles and nanoparticles;

(b) melting the ingot composition to form a melt, wherein the melt segregates into a first phase comprising the metal-containing microparticles and a second phase comprising the nanoparticles;

(c) solidifying the melt to obtain a metal matrix nanocomposite; and

(d) optionally removing a fraction of the metal matrix nanocomposite containing a lower concentration of the nanoparticles compared to the remainder of the metal matrix nanocomposite, thereby producing a master alloy metal matrix nanocomposite.

The microparticles may contain an element selected from the group consisting of Al, Mg, Ni, Fe, Cu, Ti, V, Si, and combinations thereof. The nanoparticles may contain a compound selected from the group consisting of metals, ceramics, cermets, intermetallic alloys, oxides, carbides, nitrides, borides, polymers, carbon, and combinations thereof. In certain embodiments, the microparticles contain Al, Si, and Mg, and the nanoparticles contain tungsten carbide (WC).

Step (b) may further include pressing, sintering, mixing, dispersing, friction stir welding, extrusion, binding, capacitive discharge sintering, casting, or a combination thereof. Step (b) may include holding the melt for an effective dwell time (e.g., about 1 minute to 8 hours) to cause density-driven segregation of the first phase from the second phase. Optionally, step (b) may include exposing the melt to an external force selected from gravitational, centrifugal, mechanical, electromagnetic, or a combination thereof.

Step (c) may include directional solidification or progressive solidification of the melt, if desired. Directional solidification is solidification that occurs from the farthest end of the casting and works its way towards the passage through which liquid material is introduced into a mold. Progressive solidification is solidification that starts at the walls of the casting and progresses perpendicularly from that surface.

In some embodiments, the metal-matrix phase and the first reinforcement phase are each dispersed throughout the metal matrix nanocomposite. In these or other embodiments, the metal-matrix phase and the first reinforcement phase are disposed in a layered configuration within the metal matrix nanocomposite, wherein the layered configuration includes at least a first layer comprising the nanoparticles and at least a second layer comprising the metal-matrix phase.

Step (d) may include includes machining, ablation, reaction, dissolution, evaporation, selective melting, or a combination thereof. In certain embodiments, step (d) provides two distinct master alloy metal matrix nanocomposites. A number of heating methods and dwell times are appropriate for the production of density-driven master alloy metal matrix nanocomposites.

In some embodiments, a method of fabrication of a master alloy metal matrix nanocomposite starts by using a pre-dispersed ingot as a raw material with a metal component and a reinforcing particulate. This ingot is taken to a liquid or a semi-solid phase through processing, wherein the metal component enters a molten liquid or semi-solid phase with a dispersed reinforcing component (nanoparticles).

The reinforcing component segregates through density-driven segregation, in some embodiments. In particular, the matrix is solidified and the reinforcing component is separated by density into one or more higher-volume fractions (compared to the matrix). The low-volume fraction component of the whole solid is then removed, at least partially, to leave behind a final product of a high-volume fraction master alloy metal matrix nanocomposite.

Compositions of this master alloy vary widely, according to selection of the matrix metal(s) and/or metal alloy(s) in combination with nanoparticles of arbitrary composition, including other metals or metal alloys. Reinforcing nanoparticles are preferably less than 5000 nm in size, more preferably less than 2000 nm, and most preferably less than 1000 nm, of any geometrical configuration (rod, sphere, prism, etc.). The removed low-density material may be recycled and used in subsequent processing.

The master alloy may ultimately be processed into various aluminum alloys. Such aluminum alloys may be produced by a variety of processes. Metal-part forming operations include, but are not limited to, forging, rolling, extrusion, drawing, sand casting, die casting, investment casting, powder metallurgy, additive manufacturing, or others. A cast microstructure may be desired in the final aluminum alloy, or a different microstructure may be desired, such as a forged microstructure. A cast microstructure for the master alloy may be preferred for the performance and quality of an aluminum alloy, in certain embodiments.

EXAMPLES

Materials. Aluminum alloy 7075 micropowder is purchased from Valimet Inc. (Stockton, Calif., U.S.). The powder consists of Al (balance), Zn (5.40%), Mg (2.25%), Cu (1.54%), Cr (0.19%), Fe (0.17%), Si (0.13%), Mn (0.02%), and Ti (<0.01%), in weight percent. The particle-size distribution is bimodal with peak values at 45 μm and 15 μm. Aluminum alloy 6061 micropowder is purchased from Valimet Inc. The powder consists of Al (balance), Mg (0.83%), Si (0.62%), Fe (0.25%), Cu (0.23%), Cr (0.08%), Mn (0.04%), Zn (0.04%), and Ti (0.02%), in weight percent. The average particle size is 45 μm. CL31 aluminum-silicon-magnesium alloy micropowder (AlSi10Mg) is purchased from Concept Laser (Grapevine, Tex., U.S.). The powder consists of Al (balance), Si (9.0-10.0%), Mg (0.2-0.45%), Fe (<0.55%, trace), Mn (<0.45%, trace) and Ti (<0.15%, trace), in weight percent. Particle size is optimized for selective laser melting and proprietary to the manufacturer. Hydrogen-stabilized zirconium (ZrH₂ powder) is purchased from US Research Nanomaterials Inc. (Houston, Tex., U.S.).

Selective Laser Melting. Additive manufacturing of stock aluminum alloy and functionalized aluminum alloy powders is performed on a Concept Laser M2 selective laser melting machine with single-mode, CW modulated ytterbium fiber laser (1070 nm, 400 W), scan speed up to 7.9 m/s, spot size 50 μm minimum. Powder handling parameters: 80 mm×80 mm build chamber size, 70 mm×70 mm build plate size, 20-80 μm layer thickness. The atmosphere is Ar or N₂, <0.1% O₂. Samples consist of 60 mm×20 mm×40 mm tensile block specimens and 10 mm×10 mm×40 mm blocks for examining microstructure. Samples are processed with the Concept Laser ‘islanding’ scan strategy, which was specifically developed for the CL31 AlSi10Mg alloy material to minimize thermal and residual stress build-up in the part. Islands that compose the core of the build geometry are 2 mm×2 mm in size. The 70 mm×70 mm build plates are machined out of aluminum alloy 6061 and sandblasted on the surface. Layers of the build are incremented by a range from 25 μm to 80 μm depending on part geometry and location in the build. Processing is done under a flowing, inert argon atmosphere with oxygen monitoring. All processing is completed at room temperature with no applied heat. Samples are removed from the machine and cleaned of extra powder by sonicating in water. Parts are then dried with clean, compressed, dry air.

Heat Treatment. Some samples are then heat treated to a “T6” condition, which means that these samples are solutionized at 480° C. in air with a ramp rate of 5° C./min for 2 h, then quenched with water at 25° C., and subsequently aged at 120° C. with a ramp rate of 4° C./min in air for 18 h and allowed to cool to room temperature.

Sample Preparation and Materials Characterization. All samples are removed from the build plates via wire electro discharge machining (EDM). Tensile specimens are sectioned with wire EDM to a thickness of 2 mm. Tensile specimens are prepared for mechanical testing by polishing the surfaces of the gauge section with 240, 360, 400, 800 and 1,200 grit sandpaper by hand. One side of the mechanical test samples is painted with white and spackled with black paint with an airbrush for digital image correlation using a GOM ARAIVIIS-3D Motion and Deformation Sensor. Microstructure blocks are sectioned with a water-cooled saw and mounted in epoxy resin for polishing. Grinding is done with 240, 360, 400, 800 and 1,200 grit sand paper. Final polishing of the samples is accomplished with 1-μm diamond and 50-nm Al₂O₃ polishing compounds from PACE Technologies. Some polished samples are etched with Keller's Etch for 10 s to reveal microstructure. Additional imaging is conducted using scanning electron microscopy (SEM) and electron backscatter diffraction (EBSD). To observe microstructural differences, mounted samples are observed with an optical microscope under polarized light and with SEM.

Mechanical Testing. Tensile tests are performed on a servo-electric INSTRON 5960 frame equipped with a 50-kN load cell (INSTRON). Samples are clamped by the ends of the dog-bone-shaped samples. The extension rate is 0.2 mm/min and samples are loaded until fracture. Testing is conducted following ASTM E8. A U-joint is used to account for any misalignment in the sample. Because cracking tends to orient parallel to the additive manufacturing build direction, tensile testing is conducted perpendicular to the expected crack orientation. This ensures any residual cracks have the maximum effect on the tensile properties. Observed ductility in the nanoparticle-functionalized material indicates a complete elimination of deleterious cracking.

Example 1 Grain Refinement of Pure Aluminum

In this example, tantalum (Ta) particles are added to pure aluminum as a grain refiner, and compared to pure aluminum with no Ta particle addition. The concentration of Ta in the aluminum-tantalum material is about 1 vol %. The average Ta particle size is approximately 50 nm. In both cases, the metal or functionalized metal is melted and resolidified by selective laser melting.

FIG. 6A shows an image of non-grain-refined pure aluminum 600, revealing large columnar grains 610 and cracks 620. FIG. 6B shows an image of grain-refined aluminum with Ta particles, revealing fine equated growth and a substantially crack-free microstructure.

This example demonstrates the effectiveness of grain refinement of pure aluminum using Ta addition.

Example 2 Grain Refinement of Aluminum Alloy Al 7075.

In this example, zirconium (Zr) nanoparticles are added to aluminum alloy Al 7075 as a grain refiner, and compared to pure Al 7075 with no Zr nanoparticle addition. The concentration of Zr in the functionalized alloy is about 1 vol %. The average Zr nanoparticle size is approximately 500-1500 nm. In both cases, the alloy or functionalized alloy is melted and resolidified by selective laser melting.

FIG. 7A shows an image of non-grain-refined aluminum alloy Al 7075, revealing columnar grains and significant cracking. FIG. 7B shows an image of grain-refined aluminum alloy Al 7075 with Zr particles, revealing fine equated grains and a substantially crack-free microstructure. Without being limited by theory, it is believed that Zr forms a preferred nucleating phase at sufficient concentration to reduce the critical undercooling required for equated nucleation.

It is also noted that both of FIGS. 7A and 7B (scale bars 100 μm) exhibit a characteristic structural pattern that indicates that the material was 3D-printed. The additive manufacturing process produces a unique microstructure with a weld-like pattern. There is a plurality of dendrites (from crystal growth) and grain boundaries within the microstructure. Also, the microstructures of FIGS. 7A and 7B have a crystallographic texture that is not solely oriented in the additive-manufacturing build direction. The dendrite layers have differing primary growth-direction angles with respect to each other.

FIG. 8A shows a magnified (scale bar 25 μm), polished and etched SEM image of non-grain-refined aluminum alloy Al 7075. FIG. 8B shows a magnified (scale bar 25 μm), polished and etched SEM image of grain-refined aluminum alloy, Al 7075+Zr. The microstructure of the non-grain-refined aluminum alloy Al 7075 contains large cracks, as indicated for illustration. The microstructure of grain-refined Al 7075+Zr does not contain cracks, and contains some residual porosity.

Example 3 Additive Manufacturing of Aluminum Alloy Al 7075 with Zr Grain Refiner

In this example, zirconium (Zr) nanoparticles are first added to aluminum alloy Al 7075. The concentration of Zr in the functionalized alloy is about 1 vol %. The average Zr nanoparticle size is approximately 500-1500 nm. The functionalized alloy is solution heat-treated and artificially aged, which is indicated by “T6” in the alloy name (Al 7075+Zr-T6), as described above. A control aluminum alloy, Al 7075-T6, is compared to Al 7075+Zr-T6, as is AlSi10Mg, another common alloy for comparison.

The functionalized alloy (Al 7075+Zr-T6) is 3D-printed by selective laser melting. The control alloys Al 7075-T6 and AlSi10Mg are 3D-printed with the same technique. It is believed that at least a portion of the Zr nanoparticles are in the form of Al₃Zr nucleant particles following 3D printing.

FIG. 9 shows a stress-strain curve of the functionalized aluminum alloy versus the two non-functionalized aluminum alloys, indicating significantly improved mechanical properties due to suppression of cracking in Al 7075+Zr-T6. In particular, the Al 7075+Zr-T6 alloy exhibits a tensile strength of about 440 MPa. By contrast, the Al 7075-T6 control alloy exhibits a tensile strength of about 25 MPa. Even the common additively manufactured aluminum alloy, AlSi10Mg, exhibits a tensile strength (about 310 MPa) lower than that of the Al 7075+Zr-T6 of this example.

The addition of zirconium does not substantially alter the solidification behavior at high fractions of solid, where hot tearing is typically initiated. The early inclusion of zirconium induces equated growth, which can more easily accommodate the thermal contraction strains associated with solidification. This ultimately results in an alloy system that is highly tear-resistant, despite conventional wisdom. Also, the Al 7075+Zr-T6 alloy demonstrates Lüders banding during deformation, which is indicative of an aluminum alloy with average grain sizes of less than 10 μm.

This example demonstrates that additive manufacturing of an aluminum alloy with a grain refiner increases the tensile strength significantly (almost 20× higher for Al 7075+Zr-T6 compared to Al 7075-T6). The process has been utilized to produce a 3D-printed aluminum alloy with a tensile strength over 400 MPa.

Example 4 Grain Refinement of Aluminum Alloy Al 6061

In this example, zirconium (Zr) nanoparticles are added to aluminum alloy Al 6061 as a grain refiner, and compared to pure Al 6061 with no Zr nanoparticle addition. The concentration of Zr in the functionalized alloy is about 1 vol %. The average Zr nanoparticle size is approximately 500-1500 nm. In both cases, the alloy or functionalized alloy is melted and resolidified by selective laser melting.

FIG. 10A shows an image of non-grain-refined aluminum alloy Al 6061, revealing significant cracking. FIG. 10B shows an image of grain-refined aluminum alloy Al 6061 with Zr particles, revealing fine equated grains and a substantially crack-free microstructure. These micrographs indicate essentially identical behavior compared to Al 7075 in Example 2. Without being limited by theory, it is believed that Zr forms a preferred nucleating phase (which may contain Al₃Zr) at sufficient concentration to reduce the critical undercooling required for equated nucleation.

In this detailed description, reference has been made to multiple embodiments and to the accompanying drawings in which are shown by way of illustration specific exemplary embodiments of the invention. These embodiments are described in sufficient detail to enable those skilled in the art to practice the invention, and it is to be understood that modifications to the various disclosed embodiments may be made by a skilled artisan.

Where methods and steps described above indicate certain events occurring in certain order, those of ordinary skill in the art will recognize that the ordering of certain steps may be modified and that such modifications are in accordance with the variations of the invention. Additionally, certain steps may be performed concurrently in a parallel process when possible, as well as performed sequentially.

All publications, patents, and patent applications cited in this specification are herein incorporated by reference in their entirety as if each publication, patent, or patent application were specifically and individually put forth herein.

The embodiments, variations, and figures described above should provide an indication of the utility and versatility of the present invention. Other embodiments that do not provide all of the features and advantages set forth herein may also be utilized, without departing from the spirit and scope of the present invention. Such modifications and variations are considered to be within the scope of the invention defined by the claims. 

What is claimed is:
 1. An aluminum alloy powder for manufacturing a three-dimensional high-strength aluminum alloy part by a powder bed fusion additive manufacturing process, each particle of the aluminum alloy powder comprising: an aluminum alloy including silicon, copper, and optionally magnesium, wherein, when said aluminum alloy is heated to a first temperature greater than a liquidus temperature of said aluminum alloy and subsequently cooled to a second temperature less than said liquidus temperature of said aluminum alloy and greater than a solidus temperature of said aluminum alloy, said aluminum alloy transitions from a liquid phase to a multiphase system that includes a solution of liquid phase aluminum and a solid phase of silicon particles dispersed throughout said liquid phase aluminum.
 2. The aluminum alloy powder of claim 1, wherein said copper is present in a concentration from about 0.1 wt % to about 10 wt % in said aluminum alloy.
 3. The aluminum alloy powder of claim 1, wherein said copper is present in a concentration from about 2 wt % to about 5 wt % in said aluminum alloy.
 4. The aluminum alloy powder of claim 1, wherein said copper is present in a concentration from about 3 wt % to about 4 wt % in said aluminum alloy.
 5. The aluminum alloy powder of claim 1, wherein said magnesium is present in a concentration from 0 wt % to about 2 wt % in said aluminum alloy.
 6. The aluminum alloy powder of claim 1, wherein said magnesium is present in a concentration from about 0.5 wt % to about 1 wt % in said aluminum alloy.
 7. The aluminum alloy powder of claim 1, wherein said magnesium is present in a concentration from about 0.01 wt % to about 10 wt % in said aluminum alloy.
 8. The aluminum alloy powder of claim 1, wherein said silicon is present in a concentration from about 0.01 wt % to about 20 wt % in said aluminum alloy.
 9. The aluminum alloy powder of claim 1, wherein said silicon is present in a concentration from about 0.1 wt % to about 10 wt % in said aluminum alloy.
 10. The aluminum alloy powder of claim 1, wherein said silicon is present in a concentration from about 13 wt % to about 20 wt % in said aluminum alloy.
 11. The aluminum alloy powder of claim 1, wherein said aluminum alloy further includes greater than 0 wt % and up to about 9 wt % iron, and wherein said multiphase system includes said solution of liquid phase aluminum, said solid phase of silicon particles, and another solid phase of iron-containing intermetallic particles dispersed throughout said liquid phase aluminum.
 12. The aluminum alloy powder of claim 1, wherein said aluminum alloy further includes greater than 0 wt % and up to about 5 wt % manganese.
 13. An aluminum alloy powder for manufacturing a three-dimensional high-thermal-conductivity aluminum alloy part by a powder-bed-fusion additive manufacturing process, each particle of said aluminum alloy powder comprising: an aluminum alloy including, by weight: greater than 95% aluminum, and greater than 0% and less than 5% of at least one nucleating agent, wherein, when said aluminum alloy is heated to a first temperature greater than a liquidus temperature of said aluminum alloy and subsequently cooled to a second temperature less than said liquidus temperature of said aluminum alloy and greater than a solidus temperature of said aluminum alloy, said aluminum alloy transitions from a liquid phase to a multiphase system, and wherein said multiphase system includes a solution of liquid phase aluminum and a solid phase of particles of said at least one nucleating agent dispersed throughout said liquid phase aluminum.
 14. A method of manufacturing a three-dimensional aluminum alloy part, said method comprising: (a) providing an aluminum alloy powder feed material; (b) distributing a layer of said powder feed material over a substrate; (c) scanning selective regions of said layer of said powder feed material with a high-energy laser or electron beam to form a pool of molten aluminum alloy material therein, wherein selective regions of said layer of said powder feed material corresponding to a cross-section of an aluminum alloy part being formed; (d) terminating said laser or electron beam to cool and solidify said pool of molten aluminum alloy material into a solid layer of fused aluminum alloy material; and (e) sequentially repeating steps (b) through (d) to form said aluminum alloy part made up of a plurality of solid layers of fused aluminum alloy material, wherein, during solidification of said pool of molten aluminum alloy material, solid-phase particles form within a solution of liquid phase aluminum prior to formation of solid-phase aluminum dendrites, and wherein, each of said solid layers of fused aluminum alloy material in said aluminum alloy part includes a continuous aluminum matrix phase that exhibits a crystalline structure and predominantly includes a plurality of equiaxed grains.
 15. The method of claim 14, wherein, during solidification of said pool of molten aluminum alloy material, said molten aluminum alloy material transitions from an entirely liquid phase to a multiphase system in which said solid-phase particles are dispersed throughout said solution of liquid phase aluminum.
 16. The method of claim 14, wherein said solid-phase particles serve as nuclei for subsequent formation of said solid-phase aluminum dendrites, and wherein, after said solid-phase particles form within said solution of liquid phase aluminum, said solid-phase aluminum dendrites nucleate and grow in multiple directions on said solid-phase particles.
 17. The method of claim 16, wherein growth of said solid-phase aluminum dendrites is arrested when neighboring aluminum dendrites impinge upon one another and form grain boundaries.
 18. The method of claim 14, wherein each particle of said aluminum alloy powder feed material comprises silicon, and wherein said solid-phase particles comprise particles of silicon.
 19. The method of claim 18, wherein said aluminum alloy powder feed material comprises silicon comprises from about 0.01 wt % to about 20 wt % silicon.
 20. The method of claim 19, wherein said aluminum alloy powder further comprises: greater than 0 wt % and up to 9 wt % iron; greater than 0 wt % and up to 5 wt % manganese; and silicon, wherein said solid-phase particles comprise intermetallic particles.
 21. The method of claim 19, wherein each particle of said aluminum alloy powder feed material further comprises: from about 0.1 wt % to about 10 wt % copper; and from 0 wt % to about 2 wt % magnesium.
 22. The method of claim 14, wherein each particle of said aluminum alloy powder feed material comprises, by weight: greater than 95% aluminum, and greater than 0% and less than 5% of at least one nucleating agent.
 23. The method of claim 14, wherein said at least one nucleating agent comprises at least one element or compound of titanium (Ti), boron (B), beryllium (Be), cobalt (Co), chromium (Cr), cesium (Cs), iron (Fe), hafnium (Hf), manganese (Mn), molybdenum (Mo), niobium (Nb), lead (Pb), sulfur (S), zirconium (Zr), scandium (Sc), selenium (Se), strontium (Sr), tantalum (Ta), vanadium (V), or tungsten (W).
 24. The method of claim 23, wherein said aluminum alloy powder feed material comprises greater than 0.1 wt % and less than 5 wt % Ti. 